CN108179256A - A kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product - Google Patents
A kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product Download PDFInfo
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- CN108179256A CN108179256A CN201810115005.7A CN201810115005A CN108179256A CN 108179256 A CN108179256 A CN 108179256A CN 201810115005 A CN201810115005 A CN 201810115005A CN 108179256 A CN108179256 A CN 108179256A
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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
- C21D1/78—Combined heat-treatments not provided for above
- C21D1/785—Thermocycling
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
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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
-
- 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
-
- 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
-
- 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
Abstract
The invention belongs to steel material production fields, and in particular to a kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product.The present invention is suitable for all types of Cold-Rolled TRIP Steels, it is characterised in that includes the following steps：(1) the quick heating of 2~4 cycles of Cold-Rolled TRIP Steel is quickly cooled down, and heating temperature is Ac3 to 1200 DEG C, and soaking time is 0~2s, should be cooled to room temperature TRIP steel after being quickly cooled down.(2) heat-treatment technology method based on step (1)：By the TRIP steel handled by step (1), two-phase section and held for some time are heated to, then is quickly cooled to 350~500 DEG C and held for some time, is finally cooled to room temperature TRIP steel.Compared to traditional TRIP steel heat treatment process, TRIP steel processed by the invention can significantly improve elongation percentage under the premise of tensile strength is basically unchanged, and strength and ductility product can promote more than 30%.
Description
Technical field
The invention belongs to steel material production fields, and in particular to a kind of heat treatment side for improving Cold-Rolled TRIP Steel strength and ductility product
Method.
Background technology
Environment, resource and safety problem are comed one after another with the fast development of automobile, therefore, development low stain, low oil consumption
It is had become a top priority with the automobile of high safety, this just forces some automobile production enterprises to make using high intensity, high-ductility steel plate
For body of a motor car steel.
It is well known that high intensity and high-ductility are a pair of contradictory bodies, often along with modeling while armor plate strength improves
Property significantly reduces.For automobile structure, that is, reduce formability.It is remaining difficult to understand present in steel material microscopic structure
Transformation of family name's body to martensite under stress or strain-induced effect can locally improve work hardening capacity and postpone necking down
Generation, and plasticity can be improved, which is referred to as phase change induction plasticity (Transformation-Induced
Plasticity, TRIP) effect.The TRIP steel developed using the principle has both high intensity and high-ductility, using TRIP steels
It is one of effective way of automobile lightweight to make body of a motor car.
TRIP steel can be divided into hot rolling and Cold-Rolled TRIP Steel.Cold-Rolled TRIP Steel is due to surface quality is good and thinner thickness
The advantages that, in actual production using more.General cold rolling heat treatment is divided into five stages, and quick heating, two-phase section anneal, are fast
Quickly cooling but, bainite isothermal and last cooling stage.
In traditional Cold-Rolled TRIP Steel heat treatment process, annealing temperature is selected in two-phase section, and (more than Ac1, Ac3 are hereinafter, Ac1
It is as follows with the calculation formula of Ac3) it is to obtain ferrite and austenite structure, and realize the first carburetting of austenite.
Annealing soaking time is generally more than 1min, to reach the balance of ferritic phase and austenite phase.
Ac1 (DEG C)=723-10.7Mn-13.9Ni+29Si+16.9Cr+290As+6.38W (1)
Ac3 (DEG C)=910-230C^ (1/2) -15.2Ni+44.7Si+104V+31.5Mo+13.1W (2)
The symbol of element in formula represents its content (mass fraction, %).
During subsequent austempering, partial austenitic is transformed into bainite, this process realizes Austria
Second of carburetting of family name's body so that the austenite mechanical stability not changed increases.During the heat preservation of bainite constant temperature process
Between generally more than 1min so that austenite phase mutually reaches balance with bainite.The part Ovshinsky in subsequent cooling procedure
Body is remained in the form of metastable, forms retained austenite.The microscopic structure of final cold rolling TRIP steel is ferrite+bayesian
Body+retained austenite.
The product of the strength and ductility product of steel material, i.e. tensile strength and elongation percentage is one of evaluation body of a motor car steel important
Index.Strength and ductility product is higher, illustrates that the energy absorption capability of steel material is stronger, collides the energy that absorbs in the process in automobile
Amount is higher, and the safety of automobile is better.The Cold-Rolled TRIP Steel produced through prior heat treatment process, it is residual in microscopic structure
Remaining austenite mostly in block distribution in isometric columnar ferrite grain boundaries, its mechanical stability of this she blocky type retained austenite compared with
Difference is just largely converted at the initial stage of stretcher strain for martensite, is unfavorable for the further of TRIP steel plasticity and strength and ductility product
It improves.In order to improve the plasticity of TRIP steel, people develop a kind of new heat treatment process again, the technique first to TRIP steel into
Row complete austenitizing (heat preservation more than 3min) simultaneously quenches, then the heat treatment for carrying out traditional handicraft to TRIP steel can be had
The TRIP steel of lath-shaped bainite+film-form residual austenite body tissue.Its mechanical stability of film-form retained austenite is preferable, can
Persistently to be undergone phase transition in deformation process, so as to improve the plasticity of TRIP steel, but this its tensile strength of TRIP steel is relatively low, together
Sample cannot obtain high strength and ductility product.
Invention content
In order to solve the above technical problems, the present invention is directed to the problem of existing Cold-Rolled TRIP Steel heat treatment process,
The present invention provides a kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product, in order to further improve Cold-Rolled TRIP Steel
Strength and ductility product, allow its be applied to body of a motor car when better energy absorption capability is provided.
Specific technical solution is as follows：
A kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product, follows the steps below：
(1) cycle of TRIP steel is quickly heated-is quickly cooled down, and Cold-Rolled TRIP Steel plate is heated with the rate of 20 DEG C/more than s
0~2s is kept the temperature to the Ac3~1200 DEG C short time, is cooled to room temperature again with the rate of 20 DEG C/more than s later；It is right in this approach
The cycle that TRIP steel carries out 2~4 times is quickly heated-is quickly cooled down；
(2) heat treatment process of TRIP steel two-phase section annealing+austempering based on step (1), will pass through step
Suddenly the TRIP steel plates that (1) obtains are heated to two-phase section (Ac1~Ac3) with the rate of 20 DEG C/more than s and keep the temperature 1~10min, then
350~500 DEG C are cooled to the rate of 20 DEG C/more than s and keeps the temperature 1~10min, are finally cooled to the rate of 5~20 DEG C/s
Room temperature.
The advantageous effect of this method is：
(1) existing TRIP steel heat treatments technology, the microscopic structure provided, some are isometric columnar ferrite+bainite+block
Shape retained austenite, some are ferrite bainite+film-form retained austenite, cannot significantly improve the strength and ductility product of TRIP steel.
And TRIP steel processed by the invention, ferrite and retained austenite crystal grain are more tiny, can also obtain certain volume and contain
The film-form retained austenite of amount.Film-form retained austenite can significantly improve the plasticity of Cold-Rolled TRIP Steel, but it is anti-to reduce it
Tensile strength, and tiny ferrite can then improve the intensity of TRIP steel, compensate strong as caused by there is film-form retained austenite
Degree declines.
(2) present invention can be on the basis of TRIP steel chemical compositions not be changed, hence it is evident that are improved its strength and ductility product, be applied to it
Body of a motor car is capable of providing higher energy absorption capability.
(3) heat treatment method of the invention, can be in the premise that tensile strength is basically unchanged compared with prior heat treatment process
Under significantly improve elongation percentage, strength and ductility product can promote more than 30%.
Description of the drawings
Fig. 1 is 1 heat treatment process schematic diagram of the embodiment of the present invention；
Fig. 2 is the EBSD distributed mutually figures of the embodiment of the present invention 1；
Fig. 3 is the EBSD distributed mutually figures of comparative example 1.
Specific embodiment
Below in conjunction with the heat treatment of specific embodiment and comparative example to a kind of raising Cold-Rolled TRIP Steel strength and ductility product of the present invention
Method is described in further detail.Table 1 lists the chemical composition of two kinds of TRIP steel being heat-treated using the present invention, on
It is the melting in the intermediate frequency vaccum sensitive stove of 25kg to state two kinds of Cold-Rolled TRIP Steels, cast and then carry out cogging, heating,
Hot rolling, cold rolling.The heating temperature of cogging and hot rolling is 1200 DEG C, and start rolling temperature is 1100 DEG C, and finishing temperature is 900 DEG C, heat
The final thickness for rolling plate is 5mm, and the final thickness of cold-reduced sheet is 1mm.The chemical composition one of comparative example 1,2 and embodiment 1,2,3
It causes, is the 1#TRIP steel in table 1；Comparative example 3,4 is identical with the chemical composition of embodiment 4, is the 2#TRIP steel in table 2.
The chemical composition (mass fraction, %) of Cold-Rolled TRIP Steel in 1 Examples 1 to 4 of table
Embodiment 1
The present embodiment uses the 1#TRIP steel in table 1, and the heat treatment step of the present embodiment is as follows：
(1) 2 cycles of TRIP steel are quickly heated-are quickly cooled down：On continuous annealing testing machine by TRIP steel with 50 DEG C/
The rate of s is heated to 1000 DEG C, keeps the temperature and is cooled to greenhouse with the rate of 40 DEG C/s after 2s.Above procedure recycles quick for 1 time
It heats-is quickly cooled down, carry out the cycle of 2 times to TRIP steel in total and quickly heat-be quickly cooled down.
(2) by the TRIP steel handled through step (1), two-phase section annealing+austempering is carried out：It is tried in continuous annealing
It tests and TRIP steel is heated to 810 DEG C with the rate of 40 DEG C/s on machine and keeps the temperature 5min, be cooled to 450 later with the rate of 40 DEG C/s
DEG C and keep the temperature 5min, be finally cooled to room temperature with the rate of 10 DEG C/s.
Embodiment 2
The present embodiment uses the 1#TRIP steel in table 1, and the heat treatment step of the present embodiment is as follows：
(1) 3 cycles of TRIP steel are quickly heated-are quickly cooled down：On continuous annealing testing machine by TRIP steel with 50 DEG C/
The rate of s is heated to 1000 DEG C, keeps the temperature and is cooled to greenhouse with the rate of 40 DEG C/s after 2s.Above procedure recycles quick for 1 time
It heats-is quickly cooled down, carry out the cycle of 3 times to TRIP steel in total and quickly heat-be quickly cooled down.
(2) by the TRIP steel handled through step (1), two-phase section annealing+austempering is carried out：It is tried in continuous annealing
It tests and TRIP steel is heated to 810 DEG C with the rate of 40 DEG C/s on machine and keeps the temperature 5min, be cooled to 450 later with the rate of 40 DEG C/s
DEG C and keep the temperature 5min, be finally cooled to room temperature with the rate of 10 DEG C/s.
Embodiment 3
The present embodiment uses the 1#TRIP steel in table 1, and the heat treatment step of the present embodiment is as follows：
(1) 4 cycles of TRIP steel are quickly heated-are quickly cooled down：On continuous annealing testing machine by TRIP steel with 50 DEG C/
The rate of s is heated to 1000 DEG C, keeps the temperature and is cooled to greenhouse with the rate of 40 DEG C/s after 2s.Above procedure recycles quick for 1 time
It heats-is quickly cooled down, carry out the cycle of 4 times to TRIP steel in total and quickly heat-be quickly cooled down.
(2) by the TRIP steel handled through step (1), two-phase section annealing+austempering is carried out：It is tried in continuous annealing
It tests and TRIP steel is heated to 810 DEG C with the rate of 40 DEG C/s on machine and keeps the temperature 5min, be cooled to 450 later with the rate of 40 DEG C/s
DEG C and keep the temperature 5min, be finally cooled to room temperature with the rate of 10 DEG C/s.
Embodiment 4
The present embodiment uses the 2#TRIP steel in table 1, and the heat treatment step of the present embodiment is as follows：
(1) 4 cycles of TRIP steel are quickly heated-are quickly cooled down：On continuous annealing testing machine by TRIP steel with 50 DEG C/
The rate of s is heated to 950 DEG C, keeps the temperature and is cooled to greenhouse with the rate of 40 DEG C/s after 1s.Above procedure adds for 1 the quick of cycle
Heat-be quickly cooled down in total carries out TRIP steel the cycle of 4 times and quickly heats-be quickly cooled down.
(2) by the TRIP steel handled through step (1), two-phase section annealing+austempering is carried out：It is tried in continuous annealing
It tests and TRIP steel is heated to 830 DEG C with the rate of 40 DEG C/s on machine and keeps the temperature 3min, be cooled to 400 later with the rate of 40 DEG C/s
DEG C and keep the temperature 3min, be finally cooled to room temperature with the rate of 10 DEG C/s.
Comparative example 1
This comparative example uses the 1#TRIP steel in table 1, this comparative example is with embodiment 1,2,3 difference lies in no by walking
Suddenly the processing of (1), i.e., what is do not recycled quickly heats-is quickly cooled down.Specific heat treatment step is as follows：
(1) two-phase section annealing+austempering is carried out to TRIP steel：On continuous annealing testing machine by TRIP steel with
The rate of 40 DEG C/s is heated to 810 DEG C and keeps the temperature 5min, is cooled to 450 DEG C with the rate of 40 DEG C/s later and keeps the temperature 5min, most
It is cooled to room temperature afterwards with the rate of 10 DEG C/s.
Comparative example 2
This comparative example uses the 1#TRIP steel in table 1, and the heat treatment step of this comparative example is as follows：
(1) 1 cycle of TRIP steel is quickly heated-is quickly cooled down：On continuous annealing testing machine by TRIP steel with 50 DEG C/
The rate of s is heated to 1000 DEG C, keeps the temperature and is cooled to greenhouse with the rate of 40 DEG C/s after 2s.
(2) by the TRIP steel handled through step (1), two-phase section annealing+austempering is carried out：It is tried in continuous annealing
It tests and TRIP steel is heated to 810 DEG C with the rate of 40 DEG C/s on machine and keeps the temperature 5min, be cooled to 450 later with the rate of 40 DEG C/s
DEG C and keep the temperature 5min, be finally cooled to room temperature with the rate of 10 DEG C/s.
Comparative example 3
This comparative example uses the 2#TRIP steel in table 1, and difference lies in do not pass through step with embodiment 4 for this comparative example
(1) processing, i.e., what is do not recycled quickly heats-is quickly cooled down.Specific heat treatment step is as follows：
(1) two-phase section annealing+austempering is carried out to TRIP steel：On continuous annealing testing machine by TRIP steel with
The rate of 40 DEG C/s is heated to 830 DEG C and keeps the temperature 3min, is cooled to 400 DEG C with the rate of 40 DEG C/s later and keeps the temperature 3min, most
It is cooled to room temperature afterwards with the rate of 10 DEG C/s.
Comparative example 4
This comparative example uses the 2#TRIP steel in table 1, and the heat treatment step of this comparative example is as follows：
(1) 5 cycles of TRIP steel are quickly heated-are quickly cooled down：On continuous annealing testing machine by TRIP steel with 50 DEG C/
The rate of s is heated to 950 DEG C, keeps the temperature and is cooled to greenhouse with the rate of 40 DEG C/s after 1s.Above procedure adds for 1 the quick of cycle
Heat-be quickly cooled down in total carries out TRIP steel the cycle of 5 times and quickly heats-be quickly cooled down.
(2) by the TRIP steel handled through step (1), two-phase section annealing+austempering is carried out：It is tried in continuous annealing
It tests and TRIP steel is heated to 830 DEG C with the rate of 40 DEG C/s on machine and keeps the temperature 3min, be cooled to 400 later with the rate of 40 DEG C/s
DEG C and keep the temperature 3min, be finally cooled to room temperature with the rate of 10 DEG C/s.
The mechanical property of the TRIP steel of the embodiment of the present invention 1~4 and comparative example 1~4 is listed in table 2.From table 2 it can be seen that
After 2~4 cycles are quickly heated-are quickly cooled down, then carry out the TRIP steel strength and ductility products of two-phase section annealing+austempering
Strength and ductility product compared to the TRIP steel for only passing through two-phase section annealing+austempering is obviously improved, and can at least be increased
More than 30%, and with the increase of cycle-index, strength and ductility product increases apparent.But after 1 cycle is quickly heated-is quickly cooled down,
The TRIP steel of two-phase section annealing+austempering is carried out again, and strength and ductility product improves unobvious.Through the quick heating of 5 cycles-
After being quickly cooled down, then the TRIP steel of two-phase section annealing+austempering is carried out, strength and ductility product shines quicker than through 4 cycles
Heat-be quickly cooled down+the TRIP base steels of two-phase section annealing+austempering are not originally further added by, so the quick heating of cycle-
The number being quickly cooled down is set to 2~4 times.Compared with no process cycle quickly heats-is quickly cooled down the TRIP steel of pretreatment, warp
Cycle quickly is heated-is quickly cooled down pre-process after TRIP steel its strength and ductility product the reason of significantly increasing, causing above-mentioned phenomenon be by 2
After the cycle of~4 times is quickly heated-is quickly cooled down, ferrite and retained austenite crystal grain in TRIP steel significantly refine, and
There are a certain number of film-form retained austenites to occur, the variation of this microscopic structure causes TRIP steel strength and ductility product significantly
It is promoted.Fig. 2 is the EBSD distributed mutually figures of embodiment 1, and Fig. 3 is the EBSD distributed mutually figures of comparative example 1, and the white portion in figure corresponds to
Bcc phases, i.e. ferrite and bainite, black portions correspond to fcc phases, i.e. retained austenite.From Fig. 2 and Fig. 3 it is found that embodiment 1
The retained austenite size of middle TRIP steel is more tiny, and has portion of residual austenite in film-form, this illustrates quick through 2 times
After the pretreatment heated-be quickly cooled down, the retained austenite size in TRIP steel is more tiny, and partial austenitic form is by block
Shape transformation is in film-form.TRIP steel ferrite crystal grain is 1~4 μm in embodiment 1, and ferrite crystal grain is 3~8 μm in comparative example 1,
The ferrite crystal grain of embodiment 1 is more tiny.From the point of view of mechanical property, tiny or film-form its machine of retained austenite
Tool stability is preferable, and gradual transformation occurs in deformation process, and preferable plasticity can be provided for TRIP.And small size
Ferrite can provide higher intensity, and according to Hall-Petch relational expressions, crystallite dimension is smaller, and the intensity of steel is higher, small
The ferrite crystal grain of size can make up the loss of strength as caused by there is film-form retained austenite.So as in proof strength
Under the premise of being basically unchanged, hence it is evident that improve elongation percentage and strength and ductility product, that is, improve the energy absorption capability of steel plate.
The mechanical property of TRIP steel in 2 Examples 1 to 4 of table and comparative example 1~2
Although above by specific embodiment, the present invention is described, these embodiments is not limited only to, not
Under the premise of being detached from present inventive concept, can also there are more evolutions or improved other embodiment, and these changes and improvements are all
The range that claims hereof is claimed should be belonged to.
Claims (1)
1. a kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product, it is characterised in that follow the steps below：
(1) cycle of TRIP steel is quickly heated-is quickly cooled down, and Cold-Rolled TRIP Steel plate is heated to the rate of 20 DEG C/more than s
Ac3~1200 DEG C the short time keeps the temperature 0~2s, is cooled to room temperature again with the rate of 20 DEG C/more than s later；In this approach to TRIP
The cycle that steel carries out 2~4 times is quickly heated-is quickly cooled down；
(2) heat treatment process of TRIP steel two-phase section annealing+austempering based on step (1), will pass through step (1)
The TRIP steel plates of acquisition are heated to two-phase section (Ac1~Ac3) with the rate of 20 DEG C/more than s and keep the temperature 1~10min, then with 20
DEG C/rate of more than s is cooled to 350~500 DEG C and keeps the temperature 1~10min, finally it is cooled to room temperature with the rate of 5~20 DEG C/s.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109913759A (en) * | 2019-04-02 | 2019-06-21 | 东北大学 | A kind of preparation method of twin crystal kernel structure medium managese steel material |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1985016A (en) * | 2003-01-15 | 2007-06-20 | 新日本制铁株式会社 | High-strength hot-dip galvanized steel sheet and method for producing the same |
| CN103866185A (en) * | 2014-03-14 | 2014-06-18 | 莱芜钢铁集团有限公司 | Preparation method for manufacturing low-cost ultrafine grain transformation-induced plastic steel seamless tube online |
| CN105039851A (en) * | 2015-08-17 | 2015-11-11 | 攀钢集团攀枝花钢铁研究院有限公司 | Titanium alloyed TAM steel and manufacturing method thereof |
| 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 |
| CN107475618A (en) * | 2017-07-11 | 2017-12-15 | 西南交通大学 | A kind of high tough low-carbon contains manganese deformation induced plasticity steel and preparation method in aluminium |
-
2018
- 2018-02-06 CN CN201810115005.7A patent/CN108179256A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1985016A (en) * | 2003-01-15 | 2007-06-20 | 新日本制铁株式会社 | High-strength hot-dip galvanized steel sheet and method for producing the same |
| CN103866185A (en) * | 2014-03-14 | 2014-06-18 | 莱芜钢铁集团有限公司 | Preparation method for manufacturing low-cost ultrafine grain transformation-induced plastic steel seamless tube online |
| CN105039851A (en) * | 2015-08-17 | 2015-11-11 | 攀钢集团攀枝花钢铁研究院有限公司 | Titanium alloyed TAM steel and manufacturing method thereof |
| 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 |
| CN107475618A (en) * | 2017-07-11 | 2017-12-15 | 西南交通大学 | A kind of high tough low-carbon contains manganese deformation induced plasticity steel and preparation method in aluminium |
Non-Patent Citations (1)
| Title |
|---|
| 景财年: "《相变诱发塑性钢的组织性能》", 31 August 2012, 北京：冶金工业出版社 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109913759A (en) * | 2019-04-02 | 2019-06-21 | 东北大学 | A kind of preparation method of twin crystal kernel structure medium managese steel material |
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Application publication date: 20180619 |