CN106148660A - A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel - Google Patents
A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel Download PDFInfo
- Publication number
- CN106148660A CN106148660A CN201610528117.6A CN201610528117A CN106148660A CN 106148660 A CN106148660 A CN 106148660A CN 201610528117 A CN201610528117 A CN 201610528117A CN 106148660 A CN106148660 A CN 106148660A
- Authority
- CN
- China
- Prior art keywords
- twinning
- induced plasticity
- steel
- plasticity steel
- energy
- 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
Classifications
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Forging (AREA)
Abstract
The invention discloses the preparation method of a kind of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel.Form deformed grains by middle temperature plastic working, then in Deformation structure, grow part equiax crystal by the annealing of middle temperature short time or quenching.The high density dislocation existing in deformed grains and the dislocation configuration of complexity make the external force needed for drawing process Dislocations sliding increase, therefore make the yield strength of material improve, the equiax crystal that recrystallization process is formed then promotes twinning deformation, thus ensures that material still possesses higher plasticity.The comprehensive effect of above two tissue is to make material energy absorption ability, energy absorbing efficiency and bearing capacity be improved simultaneously, and the relative scale of two kinds of tissues can be adjusted by changing plastic working and Technology for Heating Processing, thus obtains different energy absorption characteristics.Compared with common twinning-induced plasticity steel, the obtained material of the present invention has higher energy-absorbing ability, energy absorbing efficiency and bearing capacity.
Description
Technical field
The present invention relates to steel alloy manufacture field, be specifically designed a kind of deformed grains/partial, re-crystallization tissue twinning-induced
The preparation method of plasticity steel.
Background technology
High strength and ductility alloy steel or twinning-induced plasticity steel are a kind of single phase austenite steel.Because having moderate stacking fault energy and
In plastic history, sustainable formation twin gradually growing up, generation continuous print strain hardening effect, make deformation localization
Notable postponement, thus demonstrate high plasticity and high strength and ductility product (product of tensile strength and elongation after fracture), it is
The particularly pertinent novel alloy material of a kind of buffering energy-absorbing (energy-absorbing ability and energy absorbing efficiency), in Aero-Space, national defence, anti-terrorism
And the structure such as vehicle, road, bridge, building, pipeline, low-temperature storage tank has application prospect widely.Twinning-induced
The basic process of plasticity steel is: melting formation alloy under vacuum electric furnace inert atmosphere protection, forged, roll forming,
The grade axle austenite crystal of thermally treated acquisition various grain sizes again.The typical mechanical property of twinning-induced plasticity steel is: surrender
Intensity 250～350MPa, tensile strength 500～600MPa, elongation after fracture 70～85%.
Due to the performance characteristics of twinning-induced plasticity steel and application scenario with buffering energy-absorbing based on, therefore, improve its energy-absorbing
Ability, energy absorbing efficiency and bearing capacity are to improve one of its military service behavior, the basic premise expanding its range of application.We know
Road, it is bent that the energy absorbing during material stretching plastic deformation or external force make material plasticity deformation work done be equal to power-displacement
The area of line lower envelope, energy absorbing efficiency is then equal to the area ratio of this area and ideal curve envelope, and the latter is equal to maximum and draws
The product of the corresponding displacement of stretch.Therefore, briefly, the energy-absorbing ability of material to be improved and bearing capacity, need to improve it
The height of stretching force-displacement curve and length, i.e. improve its yield strength, flow stress, tensile strength and/or percentage elongation；And
The energy absorbing efficiency of material to be improved, then should improve its yield tensile ratio, i.e. improve the levelness of stretching force-displacement curve, be allowed to envelope
Geometry closer to rectangle.Improve twinning-induced plasticity steel yield strength at present and the method for tensile strength is mainly conjunction
Aurification and crystal grain refinement.Though this two kinds of methods can improve yield strength and the tensile strength of material, but is difficult to change two simultaneously
The ratio of person i.e. yield tensile ratio, therefore can not improve the energy absorbing efficiency of material.Further, since limited with strengthening mechanism by being plastically deformed
System, both approaches, while improving the strength of materials, often makes the plasticity of material be decreased obviously, counteracts to a certain extent
Intensity improves the contribution to energy-absorbing ability.For example, by control recrystallization process, the crystallite dimension of twinning-induced plasticity steel can be made
Being decreased to 0.74 μm by 35 μm, tensile strength is improved to about 900MPa by 600MPa, but elongation after fracture is declined by 72%
To about 40%, unit mass energy-absorbing is dropped to 10.2J/g by 30.6J/g, and energy absorbing efficiency is dropped to 82.1% by 87.4%.Its
Its document also reports similar result.Obviously, although twinning-induced plasticity steel can be improved by the method that crystal grain refines
Intensity and bearing capacity, but to unit mass energy-absorbing and energy absorbing efficiency significant adverse, resultant effect is still not ideal enough.Energy absorbing efficiency
It is a very important index for buffering energy-absorbing material and structure thereof.Energy absorbing efficiency is high, it is meant that same absorbing
Can use less energy-absorbing material under conditions of impact energy, beneficially optimization system designs, and mitigates construction weight, this advantage pair
For the buffering energy-absorbing structure of the delivery vehicles such as aircraft, vehicle, boats and ships particularly valuable.
It has been observed that the energy absorbing efficiency of twinning-induced plasticity steel to be improved, its yield strength should be improved and be allowed to the width improving
Degree is more than the amplification of tensile strength, to obtain the higher yield tensile ratio i.e. flow stress of higher level degree.Produce according to metal material
The dislocation movement by slip mechanism of raw surrender, the yield strength of material to be improved, must manage to increase the resistance of dislocation movement by slip and/or reduction position
Wrong dynamic property.For twinning-induced plasticity steel plastic history Dislocations, crystal boundary and twin reciprocation to material yield and
The impact of strain hardening behavior, the present invention is plastically deformed processing initially with middle temperature, it is thus achieved that dislocation density is high, the complicated (bag of configuration
Include dislocation complete a business transaction, network and climb) morphotropism soma so that stretching when dislocation mobility relatively low.Then in carrying out
Temperature annealing or quenching, the stress producing when eliminating plastic working simultaneously forms a small amount of recrystal grain, suitably reduces the tension of material
Intensity is to improve its plasticity.Combined by way of the process of low middle warm by the processing of this middle warm deformation, twinning-induced plasticity can be made
The yield strength of steel, yield tensile ratio, energy-absorbing ability and energy absorbing efficiency significantly improve.
Content of the invention
Present invention aim at providing the preparation side of a kind of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel
Method.The present invention is obtained the deformed grains with high dislocation density by middle temperature plastic working, then processes forming portion by middle warm
Divide recrystallized structure, adjusted quantity and the size of recrystal grain by changing heat treatment heating-up temperature, to change bending of material
Take intensity, tensile strength, yield tensile ratio and percentage elongation, it is achieved the raising of energy-absorbing ability, energy absorbing efficiency and bearing capacity.Side of the present invention
The twinning-induced plasticity steel that method prepares has high energy-absorbing ability, high energy absorbing efficiency and high bearing capacity.Concrete feature is as follows:
(1) main chemical compositions is (wt.%): Mn:25～35, Al:2.5～3.5, Si:2.5～3.5, C:0.02～
0.05, remaining is Fe.
(2) metallographic structure is: simple elongation and deformed austenite crystal grain arranged in parallel add the axle austenite crystals such as a small amount of,
Morphotropism grain length 10～400 μm, wide 10～20 μm；Equiax crystal diameter 5～50 μm, volume fraction 20～30%.
(3) typical case's mechanical property is: yield strength 640～700MPa, tensile strength 750～850MPa, yield tensile ratio >=
0.8, unit mass energy-absorbing 40～45J/g, energy absorbing efficiency 90～95%, elongation after fracture 40～50%.In order to realize above-mentioned mesh
, the present invention adopts the following technical scheme that
A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel, it is characterised in that include with
Lower step:
(1) melting: raw material simple substance Mn, Al, Si, C, Fe according to target composition proportion is carried out mix, former by prepare
Material is put in vacuum induction smelting furnace, carries out melting under argon shield, and melting pours into steel ingot after terminating；
(2) high temperature pulling: the steel ingot that step (1) obtains is carried out surface turnery processing, and processing capacity 2-5mm, after turning
Steel ingot pulls out through the high temperature forging of 900～1100 DEG C again, and by forging ratio 0.4-0.7, steel ingot being drawn into sectional dimension vertically is 80
The square billet of × 80mm, is then cut into the forging stock of long 550～650mm；
(3) high temperature jumping-up: jumping-up to sectional dimension is within the temperature range of 900～1100 DEG C by the forging stock of high temperature pulling
The forging stock of 120 × (120-140) mm；
(4) middle temperature pulling: the forging stock after jumping-up is pulled out within the temperature range of 600～700 DEG C to sectional dimension be 45
The forging stock of × (40-50) mm；
(5) warm process in: the forging stock after pulling is heated in resistance furnace, heating rate 9-11 DEG C/min, work as temperature
After being raised to 620～660 DEG C, quick water-cooled or naturally cool to room temperature after being incubated 0.5～1.5 hour, i.e. can get twinning-induced
Plasticity steel finished product.
The preparation method of described deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel, it is characterised in that: described
Target component be made up of following raw materials according component, each constituent mass percentage is: Mn:25～35%, Al:2.5～3.5%, Si:
2.5～3.5%, C:0.02～0.05%, remaining is Fe.
It is twinning-induced that the preparation method of described deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel processes
Plasticity steel.
Invention effect
The present invention is directed to twinning-induced plasticity steel plastic history Dislocations, crystal boundary and twin reciprocation to bend material
Clothes and the impact of strain hardening behavior, be plastically deformed processing initially with middle temperature, it is thus achieved that dislocation density is high, configuration complexity (includes
Dislocation is completed a business transaction, network and climb) morphotropism soma so that stretching when dislocation mobility relatively low.Then middle temperature is carried out
Annealing or quenching, the stress producing when eliminating plastic working simultaneously forms a small amount of recrystal grain, and the tension suitably reducing material is strong
Degree is to improve its plasticity.Combined by way of the process of low middle warm by the processing of this middle warm deformation, twinning-induced plasticity steel can be made
Yield strength, yield tensile ratio, energy-absorbing ability and energy absorbing efficiency significantly improve, the twinning-induced plasticity steel that the present invention obtains with common
The Main Mechanical contrast of twinning-induced plasticity steel is as shown in table 1.
Table 1
As can be seen from Table 1 the present invention provide make through warm forging high, middle and middle warm process twinning-induced plasticity steel, profit
With what middle warm forging appearance became, there is high density dislocation and the morphotropism soma of complicated Defect configuration, bending of material can be significantly improved
Take intensity, yield tensile ratio and energy absorbing efficiency；The appearance of partial, re-crystallization tissue, can improve the plasticity of material, thus improve its energy-absorbing
Ability, and improve while tensile strength and yield strength, then can increase the bearing capacity of material.With tradition or typically processing bar
The equiax crystal twinning-induced plasticity steel being formed under part is compared, the material that the present invention obtains can obtain simultaneously higher yield strength,
Tensile strength, yield tensile ratio, energy-absorbing ability and energy absorbing efficiency.
Brief description
Fig. 1: the typical equiaxed grain structure of common twinning-induced plasticity steel.
Typical variant crystal grain/recrystal grain the tissue of the twinning-induced plasticity steel that Fig. 2: the present embodiment obtains.
Fig. 3: the Typical tensile stress-strain diagram of common equiax crystal twinning-induced plasticity steel and performance.
The Typical tensile stress-strain diagram of the twinning-induced plasticity steel that Fig. 4: the present embodiment obtains and performance.
Detailed description of the invention
Embodiment: the twinning-induced plasticity steel of high energy-absorbing ability, high energy absorbing efficiency and high bearing capacity, its primary chemical becomes
It is divided into (wt.%): Mn:29.5；Al:2.75%；Si:3.10%；C:0.05；Remaining is Fe.
Preparation method is as follows:
(1) according to target composition carries out dispensing, carries out melting, after melting terminates in vacuum induction furnace, under argon shield
Pour into steel ingot；
(2) surface of steel ingot turnery processing amount is 2mm, after the pulling of 1000 DEG C of high temperature forgings, cutting, obtain a size of 80 ×
The forging stock of 80 × 600mm, forging ratio is 0.5；
(3) by the forging stock of high temperature pulling at the forging stock that 1000 DEG C of jumping-up to cross sectional dimensions are 120 × 120mm.
(4) at 650 DEG C, pull out the forging stock after jumping-up to the forging stock that cross sectional dimensions is 45 × 45mm；
(5) water-cooled after the forging stock after pulling being heated in resistance furnace, is incubated, 10 DEG C/min of heating rate, holding temperature
650 DEG C, temperature retention time 0.5 hour.
Mechanical performance detects: samples the forging stock after above-mentioned heat treatment, is processed into dumb-bell shape tabular tensile test bar, coupon
Length is axial with forging stock in the same direction, gauge length section a size of 6 × 2 × 40mm.
Carrying out tension test in Material Testing Machine, rate of extension is 3mm/min, records yield strength, the tension of material
Intensity and elongation after fracture.It is calculated the total energy absorbing when material is stretched to fracture according to the stretching force-displacement curve recording
Amount, then with this energy divided by the product of tensile strength and elongation after fracture, obtain energy absorbing efficiency, with this energy divided by coupon gauge length
Duan Zhiliang calculates the energy that unit mass absorbs.
Result shows, material yield strength, tensile strength and elongation after fracture be respectively as follows: 661MPa, 795MPa and
43.2% (as shown in Figure 4)；Unit mass energy-absorbing and energy absorbing efficiency be respectively as follows: 40.4J/g, 92.7%.
Claims (3)
1. the preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel, it is characterised in that include following
Step:
(1) melting: raw material simple substance Mn, Al, Si, C, Fe according to target composition proportion is carried out mix, the raw material that will prepare
Putting in vacuum induction smelting furnace, carrying out melting under argon shield, melting pours into steel ingot after terminating；
(2) high temperature pulling: the steel ingot that step (1) obtains is carried out surface turnery processing, processing capacity 2-5mm, the steel ingot after turning
Pulling out through the high temperature forging of 900 ~ 1100 DEG C, by forging ratio 0.4-0.7, steel ingot being drawn into sectional dimension vertically is 80*80mm again
Square billet, be then cut into the forging stock of long 550 ~ 650mm；
(3) high temperature jumping-up: jumping-up to sectional dimension is 120* within the temperature range of 900 ~ 1100 DEG C by the forging stock of high temperature pulling
(120-140) forging stock of mm；
(4) middle temperature pulling: the forging stock after jumping-up is pulled out within the temperature range of 600 ~ 700 DEG C to sectional dimension be 45*(40-
50) forging stock of mm；
(5) warm process in: heating the forging stock after pulling in resistance furnace, heating rate 9-11 DEG C/min, when temperature is raised to
After 620 ~ 660 DEG C, quick water-cooled or naturally cool to room temperature after being incubated 0.5 ~ 1.5 hour, i.e. can get twinning-induced plasticity steel
Finished product.
2. the preparation method of deformed grains according to claim 1/partial, re-crystallization tissue twinning-induced plasticity steel, it is special
Levying and being: described target component is made up of following raw materials according component, each constituent mass percentage is: Mn:25 ~ 35%, Al:2.5 ~
3.5%, Si:2.5 ~ 3.5%, C:0.02 ~ 0.05%, remaining is Fe.
3. the preparation method of the deformed grains described in claim 1/partial, re-crystallization tissue twinning-induced plasticity steel processes
Twinning-induced plasticity steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610528117.6A CN106148660A (en) | 2016-07-05 | 2016-07-05 | A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610528117.6A CN106148660A (en) | 2016-07-05 | 2016-07-05 | A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN106148660A true CN106148660A (en) | 2016-11-23 |
Family
ID=58061291
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610528117.6A Pending CN106148660A (en) | 2016-07-05 | 2016-07-05 | A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN106148660A (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108642404A (en) * | 2018-07-05 | 2018-10-12 | 中国科学院合肥物质科学研究院 | Antifatigue corrosion-resistant twinning-induced plasticity steel of one kind and preparation method thereof |
| CN110964892A (en) * | 2018-09-27 | 2020-04-07 | 西门子股份公司 | Method for balancing strength and ductility of metal material |
| CN111398281A (en) * | 2020-04-20 | 2020-07-10 | 西南大学 | Method for judging minimum strength area of aluminum magnesium alloy hot-rolled thick plate |
| CN111621709A (en) * | 2020-07-06 | 2020-09-04 | 中国科学院合肥物质科学研究院 | Ultrahigh-strength-plasticity-product twinning induced plasticity steel and preparation and performance regulation and control method thereof |
| CN112280941A (en) * | 2020-09-28 | 2021-01-29 | 燕山大学 | Preparation method of ultrahigh-strength ductile bainite steel based on stacking fault energy regulation |
| CN112359267A (en) * | 2020-10-27 | 2021-02-12 | 中国科学院合肥物质科学研究院 | Damping structure based on anti-fatigue twinning induced plasticity steel and preparation method |
| CN112725684A (en) * | 2020-12-30 | 2021-04-30 | 中国科学院合肥物质科学研究院 | High-damping twinning induced plasticity steel and preparation method thereof |
| CN114480980A (en) * | 2021-12-29 | 2022-05-13 | 中国铁路设计集团有限公司 | Chromium-copper alloyed weather-resistant twinning induced plasticity steel and preparation method thereof |
| CN114507770A (en) * | 2022-01-14 | 2022-05-17 | 西安建筑科技大学 | Twinning induced plasticity steel with gradient distribution of stacking fault energy and preparation method thereof |
| CN115747667A (en) * | 2022-09-07 | 2023-03-07 | 延安大学 | Coarse-grain and fine-grain uniformly-coordinated-distributed TWIP steel with composite crystal structure and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102925821A (en) * | 2012-11-28 | 2013-02-13 | 山西太钢不锈钢股份有限公司 | Steel for non-magnetic high-strength corrosion-resisting drill collar and manufacture method of steel |
| CN103866179A (en) * | 2014-02-19 | 2014-06-18 | 中国科学院合肥物质科学研究院 | High product of strength and elongation alloy steel in columnar crystal/isometric crystal composite crystal structure and preparation method thereof |
-
2016
- 2016-07-05 CN CN201610528117.6A patent/CN106148660A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102925821A (en) * | 2012-11-28 | 2013-02-13 | 山西太钢不锈钢股份有限公司 | Steel for non-magnetic high-strength corrosion-resisting drill collar and manufacture method of steel |
| CN103866179A (en) * | 2014-02-19 | 2014-06-18 | 中国科学院合肥物质科学研究院 | High product of strength and elongation alloy steel in columnar crystal/isometric crystal composite crystal structure and preparation method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 秦小梅 等: "变形温度对Fe-23Mn-2Al-0.2C TWIP钢变形机制的影响", 《金属学报》 * |
| 艾倍倍: "冷轧高锰TRIP/TWIP钢板的退火组织及其力学性能研究", 《中国优秀硕士学位论文全文数据库 工程科技Ⅰ辑》 * |
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108642404A (en) * | 2018-07-05 | 2018-10-12 | 中国科学院合肥物质科学研究院 | Antifatigue corrosion-resistant twinning-induced plasticity steel of one kind and preparation method thereof |
| CN108642404B (en) * | 2018-07-05 | 2020-06-09 | 中国科学院合肥物质科学研究院 | Fatigue-resistant corrosion-resistant twinning-induced plastic steel and preparation method thereof |
| CN110964892A (en) * | 2018-09-27 | 2020-04-07 | 西门子股份公司 | Method for balancing strength and ductility of metal material |
| CN110964892B (en) * | 2018-09-27 | 2022-02-15 | 西门子股份公司 | Method for balancing strength and ductility of metal material |
| CN111398281A (en) * | 2020-04-20 | 2020-07-10 | 西南大学 | Method for judging minimum strength area of aluminum magnesium alloy hot-rolled thick plate |
| CN111621709B (en) * | 2020-07-06 | 2021-08-24 | 中国科学院合肥物质科学研究院 | Ultrahigh-strength-plasticity-product twinning induced plasticity steel and preparation and performance regulation and control method thereof |
| CN111621709A (en) * | 2020-07-06 | 2020-09-04 | 中国科学院合肥物质科学研究院 | Ultrahigh-strength-plasticity-product twinning induced plasticity steel and preparation and performance regulation and control method thereof |
| CN112280941A (en) * | 2020-09-28 | 2021-01-29 | 燕山大学 | Preparation method of ultrahigh-strength ductile bainite steel based on stacking fault energy regulation |
| CN112359267A (en) * | 2020-10-27 | 2021-02-12 | 中国科学院合肥物质科学研究院 | Damping structure based on anti-fatigue twinning induced plasticity steel and preparation method |
| CN112359267B (en) * | 2020-10-27 | 2021-09-24 | 中国科学院合肥物质科学研究院 | Damping structure based on anti-fatigue twinning induced plasticity steel and preparation method |
| CN112725684A (en) * | 2020-12-30 | 2021-04-30 | 中国科学院合肥物质科学研究院 | High-damping twinning induced plasticity steel and preparation method thereof |
| CN114480980A (en) * | 2021-12-29 | 2022-05-13 | 中国铁路设计集团有限公司 | Chromium-copper alloyed weather-resistant twinning induced plasticity steel and preparation method thereof |
| CN114480980B (en) * | 2021-12-29 | 2023-09-08 | 中国铁路设计集团有限公司 | Chromium-copper alloyed weather-resistant twin induced plasticity steel and preparation method thereof |
| CN114507770A (en) * | 2022-01-14 | 2022-05-17 | 西安建筑科技大学 | Twinning induced plasticity steel with gradient distribution of stacking fault energy and preparation method thereof |
| CN114507770B (en) * | 2022-01-14 | 2023-12-12 | 西安建筑科技大学 | Twinning induced plasticity steel with stacking fault energy gradient distribution and preparation method thereof |
| CN115747667A (en) * | 2022-09-07 | 2023-03-07 | 延安大学 | Coarse-grain and fine-grain uniformly-coordinated-distributed TWIP steel with composite crystal structure and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106148660A (en) | A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel | |
| CA2962472C (en) | High-toughness hot-rolled high-strength steel with yield strength of grade 800 mpa and preparation method thereof | |
| RU2361931C2 (en) | Manufacturing method of sheet of austenitic iron-carbon-manganese steel with high resistance against to decelerated crack formation and sheet received by this method | |
| EP3354756B1 (en) | Online-controlled seamless steel tube cooling process and seamless steel tube manufacturing method with effective grain refinement | |
| CN104328360B (en) | Double-phase twinborn induced plastic super-strength automobile steel plate and preparation method thereof | |
| US11085098B2 (en) | Grade 550MPA high-temperature resistant pipeline steel and method of manufacturing same | |
| WO2007138752A1 (en) | High-strength steel sheet and process for producing the same | |
| CN102828109A (en) | Metastable-state phase-change plastification ultra-fine grain high-intensity plastic product steel and production method thereof | |
| CN102400036B (en) | Twin crystal induced plasticity steel with high elongation and high hole expansion rate and manufacturing method thereof | |
| CN111218620B (en) | High-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof | |
| CN107974542B (en) | A kind of grain refining preparation method of nickel-saving type two phase stainless steel | |
| CN106834942B (en) | A kind of cupric nanometer mutually strengthens medium managese steel and preparation method thereof | |
| CN107109506B (en) | The heat treatment method of manganese steel product and manganese steel product with particular alloy | |
| CN105695870A (en) | thick hot rolled sheet steel with 450MPa grade yield strength and manufacturing method thereof | |
| CN102312158A (en) | Nb, Ti alloyed low-carbon high-intensity high-plasticity TWIP steel and preparation method thereof | |
| CN106435380A (en) | Microalloyed high-aluminum high-ductility steel plate and manufacturing method thereof | |
| CN110306127A (en) | A kind of ultrahigh-intensity high-toughness steel alloy and preparation method thereof | |
| US20180216207A1 (en) | Formable lightweight steel having improved mechanical properties and method for producing semi-finished products from said steel | |
| JP5747249B2 (en) | High-strength steel material excellent in strength, ductility and energy absorption capacity and its manufacturing method | |
| EP2883974A1 (en) | Wire rod having good strength and ductility and method for producing same | |
| CN108950392B (en) | Ultrahigh-ductility low-density steel and preparation method thereof | |
| CN108728728A (en) | High manganese steel with extremely low yield ratio and manufacturing method thereof | |
| JP5483562B2 (en) | High-strength cold-rolled steel sheet with an excellent balance between elongation and stretch flangeability | |
| CN114480808A (en) | Manganese steel in composite gradient structure and preparation method thereof | |
| CN102383059A (en) | Hot rolled transformation induced plasticity (TRIP) steel and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination |