CN102925790B - Method for producing high-strength and elongation product automobile steel plate by continuous annealing technology - Google Patents
Method for producing high-strength and elongation product automobile steel plate by continuous annealing technology Download PDFInfo
- Publication number
- CN102925790B CN102925790B CN201210429409.6A CN201210429409A CN102925790B CN 102925790 B CN102925790 B CN 102925790B CN 201210429409 A CN201210429409 A CN 201210429409A CN 102925790 B CN102925790 B CN 102925790B
- Authority
- CN
- China
- Prior art keywords
- annealing
- carbide
- continuous annealing
- cold
- temperature
- 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.)
- Active
Links
Images
Abstract
The invention provides a method for producing a high-strength and elongation product automobile steel plate by a continuous annealing technology, belonging to the technical field of an automobile steel plate. The method comprises the following steps: based on the reasonable chemical component design and the alloy element partition, firstly, obtaining transition carbide with fine dispersion distribution by a cold rolled plate coil importantly, and promoting austenite inverse phase transformation through the solid solution of the fine carbide through two-phase region annealing, to obtain more and stable austenite phases to be remained. According to the method, the strict technological conditions for forming the finely-dispersed carbide and the strict interval for carrying out the technological parameters of the two-phase region annealing are given, so that the method has the advantages that the continuous annealing plate coil which is even in performance and good in surface quality can be obtained due to the short-time annealing of the existing continuous annealing production line of a steel factory, wherein the strength of the steel plate is 0.6-1.2GPa, the percentage elongation of the steel plate is 45-20%, and the product of strength and elongation is 25-40GPa%.
Description
Technical field
The invention belongs to the production technical field of automobile steel coiled sheet, particularly provide a kind of continuous annealing process to produce the method for high strength and ductility automotive sheet.By the existing continuous annealing production line of iron and steel enterprise continuous annealing in short-term (≤10 minutes), produce high strength and ductility automobile steel coiled sheet.
Technical background
High-strength high-plasticity material is pursuing a goal of persevering of material supplier author always, particularly along with the raising of automotive light weight technology and security requirement, requires automobile structure to have high strength and ductility (product of tensile strength and unit elongation) with steel.The strength and ductility product of first-generation automobile steel, in the level of 10-20GPa%, can not meet the double requirements of automotive industry future development to lightweight and high safety; People have developed TWIP steel and the austenitic steel of high-strength high-plasticity in succession in recent years, and, now by the s-generation automobile steel of appellation, their tensile strength can reach 800-1000MPa, and strength and ductility product has reached the rank of 60GPa%.But s-generation automobile steel has added the alloying elements such as a large amount of Cr, Ni, Mn, Si and Al, makes its cost higher.Due to high alloy content, caused the processing performance of steel poor, metallurgical production difficulty is larger simultaneously, thereby has limited it and produced and application.In order adapting to, to economize on resources, to reduce costs, the requirement of automotive light weight technology and raising security, need to research and develop high strength and ductility, high strength and young mobile steel cheaply.It is the high-strength high-ductility automobile steel of the third generation patent of invention of 0.02-0.50wt% C and 3.50-9.00wt%Mn that contriver team discloses main component at patent CN 101638749A, and the present invention produces the concrete production technique of this high-performing car coiled sheet by the short-cycle annealing of industrialization continuous annealing production line.
The automobile steel sheet overwhelming majority used will, by the cold rolling specific thickness that is rolled to, then produce the substrate with destination organization through continuous annealing process.But the annealing time that the continuous annealing production line of iron and steel enterprise can provide is shorter, conventionally be no more than 10 minutes, and the high-strength high-ductility automobile steel of aforementioned the invented third generation (CN 101638749A) requires annealing time sufficiently long when final annealing, so that the slower Mn of diffusion fully partition enter austenite phase, thereby obtain stable austenite, could obtain excellent mechanical property.Also be that annealing time is longer, its performance is better, but due to the restriction of production line length, its annealing time is no more than 10 minutes more on industrialized continuous annealing production line, be therefore difficult to just obtain by continuous annealing in short-term the stable austenite structure of sufficient amount.And object of the present invention is exactly by newly-designed thermal treatment process, the tissue of roll of steel plate to be carried out to pre-setting before final continuous annealing, thereby can when industrialization continuous annealing in short-term, also can obtain containing abundant and tissue stable austenite, guarantee the excellent properties of this steel.
Summary of the invention
The object of the present invention is to provide a kind of continuous annealing process to produce the method for high strength and ductility automotive sheet, by the continuous annealing production line of existing industrialization (in annealing time 10 minutes), manufacture the high-strength high-ductility automobile steel of third generation coiled sheet; Its strength and ductility product (strength and ductility product is the product of tensile strength and unit elongation) >=30GPa%.
The present invention is based on the partition of reasonable chemical composition design and alloying element, key is, before final annealing, cold rolling microstructure is carried out to pre-treatment, make the carbide particle that its diffusion-precipitation is tiny, thereby solid solution when the continuous annealing in short-term of final two-phase region, due to carbide solid solution region enrichment carbon and manganese, therefore not only provide austenite forming core core but also reduced the austenite required carbon of growing up mutually, the time of manganese partition, thereby promote to form sufficient amount and the better austenite phase of chemical stability, these austenites can remain in process of cooling, in the strain path of steel, realize TRIP or TWIP mechanism, improve plasticity and the intensity of steel.Concrete technology is as follows:
1, in the chemical composition of steel, by the further refinement of the disclosed composition range of patent CN 101638749A, be mainly 0.05-0.45wt% C and 2.50-8.00wt%Mn, P≤0.020wt%, S≤0.02wt%, remaining is Fe and inevitable impurity.Also can separately be descended a kind of or multiple element: Ni:0.1-3.0wt%, Cr:0.2-3.0wt%, Mo:0.1-0.8wt%, Si:0.3-2.3wt%, Cu:0.5-2.0wt%, B:0.0005-0.005wt%, Nb:0.02-0.10wt%, [N]: 0.002-0.25wt%, Ti:0.05-0.25wt%, V:0.02-0.25wt%, Al:0.015-0.060wt%, RE(rare earth on this basis): 0.002-0.005wt%, Ca:0.005-0.03wt%.
2, the smelting of steel with solidify: be applicable to converter, electric furnace and induction furnace and smelt, adopt continuous casting to produce strand or ingot casting is produced in die casting.
3, the hot continuous rolling after strand or ingot formation: by strand through 1100-1250 ℃ of heating, by roughing mill, carry out the rolling of 5-20 passage, hot rolling is to 30-50mm thickness specification, connects unit carry out 5-7 passage and be rolled down to after 3-15mm by heat, after rolling, at 550-700 ℃, batch, volume heavily needs to surpass more than 12 tons;
4, above-mentioned hot continuous rolling volume can annealed retarded cooling process to reduce cold rolling processing load, or without annealing, carry out, after cleanup acid treatment, at cold continuous mill group, being directly rolled after 0.6-4.0mm, obtain cold-rolled steel sheet.
5, before entering continuous annealing, the destination organization of cold-rolled steel sheet is to have size to be no more than carbide or cementite more than 25nm.According to (4), may obtain dissimilar cold rolling microstructure, the following different pretreatment technology of design obtains tiny carbide particle and separates out and the destination organization distributing;
(a) if having thick carbide or cementite (size is greater than 25nm) in cold-reduced sheet, need to utilize the continuous annealing production line of steel mill, steel plate is heated to Ac
3+ 10 to 80 ℃ are carried out first annealing, are incubated 3-10 minute with solid solution carbide or cementite, are then chilled to soon 100-400
owithin the scope of C, batch, speed of cooling is not less than 20
oc/s is to avoid entering when the slow cooling between high-temperature zone precipitated phase to thick cementite; Then roll of steel plate is hung in steel mill's holding pit or other can carry out in the equipment of temperature maintenance or the pre-treatment of tiny Carbide Precipitation is carried out in the hot blast insulation that blasts relevant temperature, maintain the temperature at 100-400
obetween C, soaking time can be between 2 minutes to 40 hours; Wherein the relation of the scope of soaking time (t, unit hour) and temperature (T, unit K) is pressed following formula (1) calculating.Soaking time is significantly different along with the difference of aging temp, because Carbide Precipitation and the remarkable temperature dependent of growing up are incubated required time and significantly shorten when temperature is higher.The object that designs this operation is exactly that timeliness by low-temperature region forms tiny carbide (<25nm), carries out C and Mn pre-concentration.When soaking time is in 10 minutes, also can adopt following technique, to be directly chilled to soon room temperature after above-mentioned austenitizing solution annealing, batch, then directly enter two-part continuous annealing furnace annealing, in the short-cycle annealing of first paragraph annealing furnace with the tiny carbide of diffusion-precipitation, annealing time 1-5 minute, annealing temperature is controlled at 300-400
oc, specifically controls numeric reference following formula (1) and calculates; And then then enter second segment continuous annealing furnace and carry out two-phase region annealing, its process parameter control is referring to step (6).
1670.66×exp(-T/64.31)-0.0008≤t≤37046×exp(-T/54.66)+0.04 （1）
(b) if not carbide-containing or cementite in cold-rolled steel coils, directly cold-rolled steel coiled sheet is hung in steel mill's holding pit or other can carry out in the equipment of temperature maintenance or the pre-treatment of separating out of carbide or cementite is carried out in the hot blast insulation that blasts relevant temperature, maintain the temperature at 100-400
obetween C, soaking time can be between 2 minutes to 40 hours; Wherein the relation of the scope of soaking time (t, unit hour) and temperature (T, unit K) is pressed above formula (1) calculating equally.When soaking time is in 10 minutes, also can adopt following technique, the cold-rolled steel coiled sheet of above-mentioned not carbide-containing is directly entered to two-part continuous annealing furnace annealing, in the short-cycle annealing of first paragraph annealing furnace with the tiny carbide of diffusion-precipitation, annealing time 1-5 minute, annealing temperature is controlled at 300-400
oc, specifically controls numeric reference (1) formula and calculates; And then then enter second segment continuous annealing furnace and carry out two-phase region annealing, its process parameter control is referring to step (6).
(c) if there is tiny carbide or cementite in cold rolling rear coil of strip, its size is less than 25nm, and cold-rolled steel coils does not need to carry out pre-treatment so, can directly carry out follow-up continuous annealing.This can improve rolling friction power by the carbides-free martensitic stucture obtaining in advance when carrying out cold continuous rolling, makes rolling band temperature remain on 100-200
othen C is with warm rolling to pick and place in heat-preserving equipment, and the time calculates by (1) formula, is less than the object of 25nm carbide to reach Precipitation size.
6, the present invention requires will after pretreated cold-rolled steel sheet winds off volume, through continuous annealing production line, carry out continuous annealing, annealing time 3-10 minute.The tiny carbide that now early stage, pre-treatment timeliness formed, can dissolve rapidly again when two-phase temperature range continuous annealing subsequently, thus accelerated austenite the formation speed of continuous annealing and Mn at austenite the enrichment speed in mutually.Although the therefore final continuous annealing time is shorter, still can form abundant and stable austenite phase.During continuous annealing, rate of heating is greater than 30
oc/s, to avoid the alligatoring of tiny carbide in heat-processed, is cooled to 450 after annealing
othe time of C is no more than 20 seconds, when avoiding austenite mutually cooling in the decomposition of high-temperature zone.Continuous annealing temperature T is the key parameter that affects final residual austenite quantity, need to strictly by following formula (2), calculate according to C in composition of steel and Mn content, cementite just can solid solution when guaranteeing to anneal at this temperature, the austenite forming mutually middle carbon content reaches maximum, therefore now the chemical stability of austenite phase is best, finally can have more austenite left behind and improve performance.
When carbon content≤0.25%,
970-12×[%wtMn]-89×[%wtC]≤T(K) ≤1030-12×[%wtMn]-89×[%wtC] (2a)
When carbon content >0.25%
950-12×[%wtMn]+24×[%wtC]≤T(K) ≤1005-12×[%wtMn]+24×[%wtC] (2b)
7, the continuous annealing roll of steel plate of preparing by this technology, its intensity is 0.6-1.2GPa, and unit elongation is 45-25%, and strength and ductility product is 30-40GPa%.
Can also further improve or reach performance by following technology on the basis of the above: 1, can add Ni, Mo, Cr, B etc. and further improve the refinement original austenite grains such as the hardening capacity of steel or low-temperature impact toughness, interpolation Nb, V, Ti, add Cu, V etc. and by precipitation strength, improves the intensity of steel and add the raisings intensity such as Si and inhibition Carbide Precipitation etc., interpolation [N] regulate austenitic stability etc.; 2, by rolling technologys such as hot rolling or warm-rollings, control the homogeneity of the heterogeneous microstructure of steel, refining grain size, for final thermal treatment provides desirable weave construction; 3, the technique of this patent invention is equally applicable to continuous annealing-galvanization production line, coil of strip after continuous annealing at 350-500
oc temperature range is carried out pot galvanize through zinc pot, thereby produces hot-dip galvanizing sheet steel.The concept that the present invention proposes and pretreatment technology are applicable to the production of the production of high-performance cold rolled and hot-rolled high-strength auto sheet, high-performance section bar and excellent wire rod etc. under existing industrial condition too, also be applicable to realize high performance product by thermal treatment means, as thermoforming part etc.
Accompanying drawing explanation
Fig. 1 is that cold rolled strip coil (the C composition in table 1) is through 780
othen C continuous annealing be cooled to differing temps insulation different time (the different pretreatments technique shown in table 2), finally by rear 650 with carbide or cementite in austenitizing solid solution cold rolling microstructure in 10 minutes
oresidual austenite mark in the steel of C continuous annealing after 5 minutes, X-ray diffraction survey sheet.
Fig. 2 is that C component steel causes separating out the relatively thick cementite particle of size through pretreatment technology 2, its subsequently 650
ocannot solid solution in minute annealing of C * 5.Transmission electron microscope light field photo
Fig. 3 is that C component steel causes separating out the relatively thick cementite particle of size through pretreatment technology 2, its subsequently 650
ocannot solid solution in minute annealing of C * 5.Transmission electron microscope details in a play not acted out on stage, but told through dialogues photo, the corresponding photo that is the same area with Fig. 2.
Fig. 4 is that C component steel causes separating out the relatively thick cementite particle of size through pretreatment technology 1, its subsequently 650
ocannot solid solution in minute annealing of C * 5.Transmission electron microscope light field photo
Fig. 5 is that C component steel causes separating out the relatively thick cementite particle of size through pretreatment technology 1, its subsequently 650
ocannot solid solution in minute annealing of C * 5.Transmission electron microscope details in a play not acted out on stage, but told through dialogues photo, the corresponding photo that is the same area with Fig. 4
Embodiment
Embodiment:
The present embodiment test adopts the tri-kinds of chemical compositions of A, B, C shown in table 1, by induction furnace, is smelted, and casting ingot-forming after heat is swaged into the slab that 50mm is thick, then in warp, tries out the hot rolled coil that single stand mill is rolled to 6mm, controls finishing temperature 750
oc left and right, coiling temperature >600
oc, put into holding furnace insulation 5 hours subsequently stove be chilled to room temperature, then by hot rolled coil through rolled by cold rolling machine to 2mm.The subsequent anneal of cold-reduced sheet completes on the annealing simulation machine in laboratory.Cold-rolled steel sheet is first 780
oc anneals 6 minutes with austenitizing solid solution carbide, by being not less than 20
oc/s is cooled to differing temps, according to 8 kinds of pretreatment technology shown in table 2, carries out pre-treatment.Wherein 550
oc and room temperature heat preservation method are for comparing technique.Finally will be heated to 650 through the pretreated cold rolled strip coil of above-mentioned different process
o5 minutes rapid cooling of C annealing (are not less than 20
oand measure residual austenite mark (Fig. 1) and the mechanical property (table 3) in its finished product C/s).The explication de texte of tissue characterizes to be found, if 550
oc insulation several minutes, can cause separating out the relatively thick cementite of size (>30nm) and these cementites final 650
oc annealing 5 minutes cannot solid solution, as shown in Figure 2, because these cementite enrichment carbon and manganese, thereby cause the rich manganese of formation and the minimizing of the austenite phase amount of carbon and poor chemical stability when annealing, so final residual austenite minimum number, as shown in Figure 1, corresponding performance also the poorest (shown in table 3).And pass through 100-400
othe insulation of C is processed and is separated out after tiny carbide, subsequently 650
oc these tiny carbide of when annealing can solid solution, has so just realized the pre-concentration of carbon and manganese, thereby has accelerated 650
othe formation speed of the austenite phase in C when annealing has strengthened the chemical stability of austenite phase simultaneously due to the further enrichment of manganese.The steel of therefore separating out processing through carbonization at low temperature thing is with respect to the steel without separating out processing, 650
oresidual austenite quantity after C annealing is many, almost increases by 10% left and right, so mechanical mechanics property improvement, even if be annealing in of short duration 5 minutes, its mechanical property has also reached the standard of third generation automobile steel.In addition, experimental result is found, when pretreatment temperature is low to moderate 100
oduring C, the impact of soaking time diminishes, and this means that this process window is wide in range, is easy in industrial realization.
The chemical composition of table 1 invention steel
Pretreatment technology before the final continuous annealing of table 2
The steel plate of composition shown in table 3 table 1 pretreatment technology in 8 shown in table 2 again after austenitizing annealing, finally by 650
othe mechanical property of the steel plate after minute annealing of C * 5
Claims (3)
1. a continuous annealing process is produced the method for high strength and ductility automotive sheet, converter, electric furnace or induction furnace are smelted, and steel plate chemistry becomes 0.05-0.45wt%C, 2.50-8.00wt%Mn, P≤0.020wt%, S≤0.02wt%, remaining is Fe and inevitable impurity; The technical parameter of processing step and control is:
(1) smelting of steel with solidify: be applicable to converter, electric furnace and induction furnace and smelt, adopt continuous casting to produce strand or ingot casting is produced in die casting;
(2) hot continuous rolling after strand or ingot formation: by strand through 1100-1250 ℃ of heating, by roughing mill, carry out the rolling of 5-20 passage, hot rolling is to 30-50mm thickness specification, connects unit carry out 5-7 passage and be rolled down to after 3-15mm by heat, after rolling, at 550-700 ℃, batch, volume heavily needs to surpass more than 12 tons;
(3) above-mentioned hot continuous rolling is rolled up annealed retarded cooling process to reduce cold rolling processing load, or without annealing, carries out, after cleanup acid treatment, at cold continuous mill group, being directly rolled after 0.6-4.0mm, obtains cold-rolled steel sheet;
(4) before entering continuous annealing, the destination organization of cold-rolled steel sheet is to have size to be no more than carbide or cementite more than 25nm; According to (3), obtain dissimilar cold rolling microstructure, the following different pretreatment technology of design obtains tiny carbide particle and separates out and the destination organization distributing;
In cold-reduced sheet, there is size to be greater than carbide or the cementite of 25nm, need to utilize the continuous annealing production line of steel mill, steel plate is heated to Ac3+10 to 80 ℃ and carries out first annealing, be incubated 3-10 minute with solid solution carbide or cementite, then be chilled within the scope of 100-400 ℃ and batch, speed of cooling is not less than 20 ℃/s to avoid entering when the slow cooling between high-temperature zone precipitated phase to thick cementite; Then the pre-treatment of tiny Carbide Precipitation is carried out in the hot blast insulation that roll of steel plate is hung in holding pit or blast relevant temperature, maintains the temperature between 100-400 ℃, and soaking time is between 2 minutes to 40 hours; Soaking time t wherein, the relation of temperature T is pressed following formula (1) and is calculated; When soaking time is in 10 minutes, after above-mentioned austenitizing solution annealing, being directly chilled to soon room temperature batches, then directly enter two-part continuous annealing furnace annealing, in the short-cycle annealing of first paragraph annealing furnace with the tiny carbide of diffusion-precipitation, annealing time 1-5 minute, annealing temperature is controlled at 300-400 ℃, specifically controls numerical value and calculates by formula (1); And then then enter second segment continuous annealing furnace and carry out two-phase region annealing, it is controlled by step (5);
1670.66×exp(-T/64.31)-0.0008≤t≤37046×exp(-T/54.66)+0.04 （1）
Wherein, the unit hour of t, the unit K of T,
Not carbide-containing or cementite in cold-rolled steel coils, the pre-treatment of separating out of carbide or cementite is carried out in the hot blast insulation that directly cold-rolled steel coiled sheet is hung in holding pit or blast relevant temperature, maintain the temperature between 100-400 ℃, soaking time is between 2 minutes to 40 hours; Wherein the relation of soaking time t and temperature T is pressed above formula (1) calculating; When soaking time is in 10 minutes, the cold-rolled steel coiled sheet of above-mentioned not carbide-containing is directly entered to two-part continuous annealing furnace annealing, in the short-cycle annealing of first paragraph annealing furnace with the tiny carbide of diffusion-precipitation, annealing time 1-5 minute, annealing temperature is controlled at 300-400 ℃, specifically controls numerical value and calculates by (1) formula; And then then enter second segment continuous annealing furnace and carry out two-phase region annealing, it is controlled by step (5);
In coil of strip, had tiny carbide or cementite after cold rolling, its size is less than 25nm, and cold-rolled steel coils does not need to carry out pre-treatment so, directly carries out follow-up continuous annealing; By the carbides-free martensitic stucture obtaining in advance when carrying out cold continuous rolling, improve rolling friction power, make rolling band temperature remain on 100-200 ℃ and be then with warm rolling to pick and place in heat-preserving equipment, the time calculates by (1) formula, is less than the object of 25nm carbide to reach Precipitation size;
(5) will after winding off volume, pretreated cold-rolled steel sheet carry out continuous annealing through continuous annealing production line, annealing time 3-10 minute; During continuous annealing, rate of heating is greater than 30 ℃/s, and to avoid the alligatoring of tiny carbide in heat-processed, the time that is cooled to 450 ℃ after annealing is no more than 20 seconds, when avoiding austenite mutually cooling in the decomposition of high-temperature zone; Continuous annealing temperature T is the key parameter that affects final residual austenite quantity, need to strictly by following formula (2), calculate according to C in composition of steel and Mn content,
When carbon content≤0.25%,
970-12 * [%wtMn]-89 * [%wtC]≤T (K)≤1030-12 * [%wtMn]-89 * [%wtC] is (2a) when carbon content >0.25%
950-12×[%wtMn]+24×[%wtC]≤T(K)≤1005-12×[%wtMn]+24×[%wtC] (2b)
Prepared continuous annealing roll of steel plate, its intensity is 0.6-1.2GPa, and unit elongation is 45-25%, and strength and ductility product is 30-40GPa%.
2. method according to claim 1, it is characterized in that, described steel plate chemical composition is separately descended a kind of or multiple element: Ni:0.1-3.0wt%, Cr:0.2-3.0wt%, Mo:0.1-0.8wt%, Si:0.3-2.3wt%, Cu:0.5-2.0wt%, B:0.0005-0.005wt%, Nb:0.02-0.10wt%, [N]: 0.002-0.25wt%, Ti:0.05-0.25wt%, V:0.02-0.25wt%, Al:0.015-0.060wt%, RE:0.002-0.005wt%, Ca:0.005-0.03wt%; Described carbide is cementite.
3. method according to claim 1, is characterized in that, after continuous annealing, the zinc pot that its annealed sheet steel involves in into 350-500 ℃ carries out pot galvanize, to obtain automobile hot-galvanized steel coiled sheet.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210429409.6A CN102925790B (en) | 2012-10-31 | 2012-10-31 | Method for producing high-strength and elongation product automobile steel plate by continuous annealing technology |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210429409.6A CN102925790B (en) | 2012-10-31 | 2012-10-31 | Method for producing high-strength and elongation product automobile steel plate by continuous annealing technology |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102925790A CN102925790A (en) | 2013-02-13 |
| CN102925790B true CN102925790B (en) | 2014-03-26 |
Family
ID=47640713
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201210429409.6A Active CN102925790B (en) | 2012-10-31 | 2012-10-31 | Method for producing high-strength and elongation product automobile steel plate by continuous annealing technology |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102925790B (en) |
Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104233059A (en) * | 2013-06-19 | 2014-12-24 | 鞍钢股份有限公司 | Delayed-fracture-resistant high-strength TWIP steel |
| EP3029162B1 (en) | 2014-12-01 | 2018-04-25 | Voestalpine Stahl GmbH | Method for the heat treatment of a manganese steel product |
| CN104694816A (en) * | 2015-03-13 | 2015-06-10 | 北京科技大学 | Preparation method of high-Al medium manganese steel with strength and ductility product exceeding 30GPa% |
| CN106244918B (en) * | 2016-07-27 | 2018-04-27 | 宝山钢铁股份有限公司 | A kind of 1500MPa grades of high strength and ductility automobile steel and its manufacture method |
| CN107794357B (en) * | 2017-10-26 | 2018-09-14 | 北京科技大学 | The method of super rapid heating technique productions superhigh intensity martensite cold-rolled steel sheet |
| CN109837470B (en) * | 2017-11-29 | 2022-04-01 | 宝钢德盛不锈钢有限公司 | High-strength nitrogen-containing economical austenitic stainless steel and manufacturing method thereof |
| CN107974631B (en) * | 2017-12-01 | 2019-07-30 | 安徽工业大学 | A kind of method of various dimensions enhancing plasticising production high strength and ductility superhigh intensity third generation automobile steel |
| CN109082590A (en) * | 2018-08-23 | 2018-12-25 | 东北大学 | A kind of high-strength plasticity hot rolling medium managese steel plate and its critical zone roll preparation method |
| CN110964882B (en) * | 2019-11-27 | 2021-11-02 | 本钢板材股份有限公司 | One-steel dual-purpose cold-rolled high-strength steel based on carbon distribution process and manufacturing method thereof |
| CN113801984B (en) * | 2020-06-15 | 2023-03-21 | 中国科学院金属研究所 | Plastic deformation processing technology for synchronously improving strength and plasticity of low-carbon steel |
| CN115747669B (en) * | 2022-11-16 | 2023-11-17 | 华北理工大学 | Aluminum-containing medium manganese steel with 980 MPa-level high-strength plastic product and preparation method thereof |
Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1992002652A1 (en) * | 1990-08-04 | 1992-02-20 | Nkk Corporation | Damping alloy |
| US6387192B1 (en) * | 1997-07-01 | 2002-05-14 | Georg Frommeyer | Light constructional steel and the use thereof |
| WO2005061152A1 (en) * | 2003-12-23 | 2005-07-07 | Salzgitter Flachstahl Gmbh | Method for the generation of hot strips of light gauge steel |
| CN101660086A (en) * | 2008-08-25 | 2010-03-03 | 鞍钢股份有限公司 | Light and high-performance twin crystal inducing plasticity steel and preparation method thereof |
| CN101956134A (en) * | 2010-11-01 | 2011-01-26 | 福州大学 | High-strength high-plasticity copper-containing high-carbon TWIP steel and preparation process thereof |
| CN102011051A (en) * | 2010-11-29 | 2011-04-13 | 上海大学 | High-strength and high-ductility medium carbon TRIP (transformation induced plasticity) steel and preparation method thereof |
| CN102021472A (en) * | 2011-01-12 | 2011-04-20 | 钢铁研究总院 | Production method for continuous annealing process high strength and plasticity product automobile steel plate |
| CN102199722A (en) * | 2011-05-09 | 2011-09-28 | 北京科技大学 | Transformation induced plasticity (TRIP) steel plate of bainite substrate and preparation method thereof |
| CN102212746A (en) * | 2011-06-03 | 2011-10-12 | 武汉钢铁(集团)公司 | Twin crystal induced plastic steel with strength-plasticity product of more than 65GPa percent and production method thereof |
| CN102304664A (en) * | 2011-09-13 | 2012-01-04 | 北京科技大学 | High strength and high plasticity aluminum-containing medium manganese transformation-induced plasticity (TRIP) cold-rolled steel plate and preparation method thereof |
-
2012
- 2012-10-31 CN CN201210429409.6A patent/CN102925790B/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1992002652A1 (en) * | 1990-08-04 | 1992-02-20 | Nkk Corporation | Damping alloy |
| US6387192B1 (en) * | 1997-07-01 | 2002-05-14 | Georg Frommeyer | Light constructional steel and the use thereof |
| WO2005061152A1 (en) * | 2003-12-23 | 2005-07-07 | Salzgitter Flachstahl Gmbh | Method for the generation of hot strips of light gauge steel |
| CN101660086A (en) * | 2008-08-25 | 2010-03-03 | 鞍钢股份有限公司 | Light and high-performance twin crystal inducing plasticity steel and preparation method thereof |
| CN101956134A (en) * | 2010-11-01 | 2011-01-26 | 福州大学 | High-strength high-plasticity copper-containing high-carbon TWIP steel and preparation process thereof |
| CN102011051A (en) * | 2010-11-29 | 2011-04-13 | 上海大学 | High-strength and high-ductility medium carbon TRIP (transformation induced plasticity) steel and preparation method thereof |
| CN102021472A (en) * | 2011-01-12 | 2011-04-20 | 钢铁研究总院 | Production method for continuous annealing process high strength and plasticity product automobile steel plate |
| CN102199722A (en) * | 2011-05-09 | 2011-09-28 | 北京科技大学 | Transformation induced plasticity (TRIP) steel plate of bainite substrate and preparation method thereof |
| CN102212746A (en) * | 2011-06-03 | 2011-10-12 | 武汉钢铁(集团)公司 | Twin crystal induced plastic steel with strength-plasticity product of more than 65GPa percent and production method thereof |
| CN102304664A (en) * | 2011-09-13 | 2012-01-04 | 北京科技大学 | High strength and high plasticity aluminum-containing medium manganese transformation-induced plasticity (TRIP) cold-rolled steel plate and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102925790A (en) | 2013-02-13 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102925790B (en) | Method for producing high-strength and elongation product automobile steel plate by continuous annealing technology | |
| CN103556048B (en) | Production method for two-phase automobile steel plate with low yield-strength ratio and high strength | |
| CN106086640B (en) | A kind of cold rolling medium managese steel and preparation method thereof of superhigh intensity plasticity product | |
| CN104328360B (en) | Double-phase twinborn induced plastic super-strength automobile steel plate and preparation method thereof | |
| CN101713046B (en) | Preparation method of superfine grain martensitic steel reinforced and controlled by nano precipitated phase | |
| CN102839329B (en) | Cold-rolling double-phase-steel steel plate with tensile strength of 450 MPa, and preparation method thereof | |
| CN107127212B (en) | The method that super rapid heating technique produces manganese cold-rolled steel sheet in high strength and ductility | |
| CN101580916B (en) | High-strength high-plasticity twinning-induced plasticity steel and manufacturing method thereof | |
| CN106191390B (en) | A kind of middle manganese TRIP steel and preparation method thereof | |
| CN111996467B (en) | 980 MPa-grade galvanized high-strength steel and preparation method thereof | |
| CN102304664A (en) | High strength and high plasticity aluminum-containing medium manganese transformation-induced plasticity (TRIP) cold-rolled steel plate and preparation method thereof | |
| CN103255341B (en) | High-strength and high-toughness hot-rolled wear-resistant steel and preparation method thereof | |
| CN110073026B (en) | High-strength cold-rolled steel sheet and hot-dip galvanized steel sheet having excellent yield strength, ductility and hole expansibility, and methods for producing same | |
| CN102400053B (en) | Steel plate for building structure with yield strength of 460 MPa, and manufacturing method thereof | |
| CN104928456B (en) | A kind of manufacture method for improving general chill ferritic lightweight steel ductility | |
| CN103060678A (en) | Medium temperature deformation nanometer austenite enhanced plasticized steel and preparation method thereof | |
| CN104498821B (en) | Medium-manganese high-strength steel for automobiles and production method thereof | |
| CN102021472A (en) | Production method for continuous annealing process high strength and plasticity product automobile steel plate | |
| CN104593675A (en) | Preparation method of metal material with TWIP (twinning induced plasticity) and TRIP (transformation of retained austenite induced plasticity) effects | |
| CN103469089B (en) | A kind of cheese crystal grain deep-draw dual phase sheet steel and preparation method thereof | |
| CN104254630A (en) | Cold-rolled steel sheet and manufacturing method for same | |
| CN102021483B (en) | Cold-rolled dual-phase steel plate with 1,200 MPa-level tensile strength and preparation method thereof | |
| CN102140609A (en) | Composite silicon and aluminum-added 590MPa-level transformation-induced plasticity steel and preparation method | |
| CN103938070A (en) | Steel plate and preparation method thereof | |
| CN109680130A (en) | A kind of high strength and ductility cold rolling medium managese 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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |