CN101225459A - Method for manufacturing high-plastic ultra-fine grain micro-alloy low-carbon steel - Google Patents
Method for manufacturing high-plastic ultra-fine grain micro-alloy low-carbon steel Download PDFInfo
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- CN101225459A CN101225459A CNA2008100091359A CN200810009135A CN101225459A CN 101225459 A CN101225459 A CN 101225459A CN A2008100091359 A CNA2008100091359 A CN A2008100091359A CN 200810009135 A CN200810009135 A CN 200810009135A CN 101225459 A CN101225459 A CN 101225459A
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Abstract
The invention discloses a manufacturing method of high plastic ultra-fine grain microalloy low carbon steel, which is characterized in that: a. the 14MnNb steel hot-rolled plate is heated to 950 to 1020 degrees and keeps a constant temperature in the range of 950 to 1020 DEG C for 30 to 40 minutes; b. the hot-rolled plate is cooled to 840 to 800 degrees C as furnace cooling and keeps a constant temperature in the range of 840 to 800 degrees C for 30 to 40 minutes and then is put into 10 percent brine to quench; c. total reduction amount 60 to 80 percent multi-pass ambient temperature rolling deformation is carried out; d. the temperature is kept at 500 to 600 degrees C for 1 to 20 hours, and then the plate is air cooled, recrystallized and annealed. The manufacturing method of high plastic ultra-fine grain microalloy low carbon steel, has the advantages that: the high plastic ultra-fine grain microalloy low carbon steel prepared has high strength and larger elongation of 11.3 percent, and the tensile strength is 615MPa, compared with the ultra-fine grain obtained by deformation, recrystallization and annealing of pure martensite, the elongation and the tensile strength is respectively increased for 85 percent and 23 percent. The manufacturing method is suitable for producing high plastic ultra-fine grain microalloy low carbon steel plate or strip steel rolled stock.
Description
Technical field
The present invention relates to a kind of manufacture method of ultra fine grain low-carbon steel, particularly relate to a kind of manufacture method with ultra-fine grain micro-alloy low-carbon steel of high-ductility.
Background technology
Ultrafine Grained Steel has high tensile strength, has been subjected to the extensive concern of material educational circles in recent years.The material supply section scholar has carried out a large amount of deep researchs in the preparation method and the fields such as tissue and performance characteristics of Ultrafine Grained Steel.Existing report, utilize the cold rolling back recrystallization annealing of full martensitic stucture can successfully prepare ultra fine grain low-carbon steel (Scr.Mater.2002, Vol.47, p.893) and nanocrystalline soft steel (Mater.Sci.Eng.A, 2006, Vol.432, p.216).Studies show that along with reducing of grain-size, work hardening capacity and tensile elongation reduce, occur the plastic instability phenomenon (Mater.Sci.Eng.A, 2000, Vol.293, p.165; Scr.Mater.2002, Vol.47, p.893; Acta Mater.2005, Vol.52, p.4881; Scr.Mater.2005, Vol.52, p.1039).This has greatly limited the processing and the practical application of Ultrafine Grained Steel.Therefore, improve the focus that Ultrafine Grained Steel plasticity has become the ferrous materials research field.At present super fine crystal material plasticity and the low major cause of work hardening capacity are, crystal grain is tiny cause dislocation not accumulate and dislocation saturated (Appl.Phys.Lett.2001, Vol.79, p.611; Nat.Mater.2004, Vol.3, p.351; Science, 2004, Vol.304, p.273).An effective means that improves ultra-fine crystalline substance or nanocrystalline non-ferrous metal and alloy plasticity and seldom reduce intensity be bimodal grain size distribution (Nature, 2002, Vol.419, p.912; Scr.Mater.2003, Vol.49, p.297; Scr.Mater.2003, Vol.49, p.657; Scr.Mater.2004, Vol.51, p.795; Acta Mater.2004, p.1699) Vol.52, promptly dopes bigger crystal grain in the matrix of ultra-fine crystalline substance.And at present the method for the raising Ultrafine Grained Steel plasticity of report mainly be utilize the cementite particle of introducing the nanoscale that disperse distributes (Scr.Mater.2002, Vol.46, p.305; Scr.Mater.2005, Vol.52, p.1075; Scr.Mater.2006, Vol.54, p.1385).The contriver uses for reference this method that improves ultra-fine brilliant non-ferrous metal and alloy plasticity, infer that bimodal grain size distribution also can be used to improve the plasticity of ultra fine grain low-carbon steel, and obtain the method for bimodal grain size distribution ultrafine-grained (UFG) microstructure at the 20CrMnTi steel, obtain a national inventing patent (ZL 200410104244.0), its method is: be heated to two-phase region temperature predeformation quenching+room temperature compression set+recrystallization annealing.So can obtain " ferrite of bimodal grain size distribution+nano silicon carbide composition granule " tissue.Not long ago, (Scr.Mater.2007 such as H.Azizi-Alizamini, Vol.57, p.1065) reported that the method with " complete austenitizing quenching+subcritical quenching+50% cold rolling+recrystallization annealing " has obtained bimodal grain size distribution ferritic structure in soft steel, tensile stress-strain curve shows continuous surrender, compare with the tensile property after complete martensite 50% rolling back recrystallize is handled, intensity and plasticity are all close, have avoided L ü ders strain to produce.In view of this, distribute with bimodal ferrite grain size that to improve ultra fine grain low-carbon steel plasticity be feasible.
Summary of the invention
In order under condition, to improve the plasticity of ultra-fine grain micro-alloy low-carbon steel than small loss intensity, the invention provides a kind of manufacture method of high-plastic ultra-fine grain micro-alloy low-carbon steel, this high-plastic ultra-fine grain micro-alloy low-carbon steel keeps high-intensity to have simultaneously than high elongation rate.[p.1065] Bao Dao processing method is compared for Scr.Mater.2007, Vol.57, has cancelled high temperature predeformation and quench treatment in advance respectively for this processing method and Chinese invention patent ZL 200410104244.0 and document.The present invention can produce the ultra-fine grain micro-alloy low-carbon steel sheet material with excellent comprehensive mechanical property economically.
The technical solution adopted for the present invention to solve the technical problems is:
A. the 14MnNb steel hot-rolled sheet is heated in 950～1020 ℃ of temperature ranges and is incubated 30～40min;
B. in 10% salt solution, quench behind ℃ insulation 30～40min of furnace cooling to 840～800;
C. carry out the multi-pass room temperature rolling deformation of total reduction 60～80% then;
D carries out the recrystallization annealing of 500～600 ℃ of insulation 1～20h air coolings at last again.
The invention has the beneficial effects as follows: gained ultrafine-grained (UFG) microstructure is the mixed structure of submicron and a small amount of several microns ferrite crystal grain, and nano silicon carbide composition granule that distributing on it.Utilize the subcritical quenching of soft steel to obtain " ferrite+martensite " tissue, martensite carbon content height in the cold roller and deformed back recrystallization annealing process, and easily separate out nano-carbide, carry out thereby hinder recrystallize, so recrystallize speed is slower; And the low recrystallize speed of ferrite carbon content wants fast relatively, so can cause the bimodal distribution feature of final ferrite grain size; Carry out the tensile property test and obtain full martensitic stucture sample cold roller and deformed and recrystallization annealing comparing with 950 ℃ of quenchings, elongation than complete martensite deformation at room temperature after the ultrafine-grained (UFG) microstructure that obtains of recrystallization annealing improve approximately 85%, and tensile strength improves about 75% than supply of material state.
Description of drawings
Fig. 1 is the tensile stress-strain curve of 14MnNb micro-alloy low-carbon steel after 70% cold rolling+580 ℃ annealing 120min handles of different quenching structures.
In Fig. 1, (a) corresponding 950 ℃ of quenchings obtain full martensitic stucture; (b) corresponding 950 ℃ of austenitizing stoves are as cold as 830 ℃ of insulation 30min quenching and obtain martensite+ferritic structure.
Embodiment
Embodiment: the 14MnNb hot-rolled steel sheet that 14mm is thick is cut into sheet shears and is of a size of the tabular of 120 * 30mm, and length direction is along rolling direction.Cut at 1/2 thickness place along parallel plate face direction with the line cutting, obtain the plate tensile sample of two 120 * 30 * 7mm.With resistance furnace two plate samples are heated to 950 ℃ of insulation 30min, first sample directly quenches in 10% salt solution, behind second sample furnace cooling to 830 ℃ insulation 30min, quenches in 10% salt solution.Thick to 5mm this two quenching samples ground finish with grinding machine then, it is cold rolling to carry out multi-pass again, and total reduction 70% is again at 580 ℃ of annealing 120min.After the processing, carry out structure observation and stretching experiment., measure and the statistics grain size distribution perpendicular to the microtexture of rolling with transmission electron microscope observing to the cross section.The result shows, obtains directly through being the ferrite crystal grain of 50～200nm after first sample is cold rolled annealed, and the nano silicon carbide composition granule is distributing; Obtain the ferrite crystal grain that diameter is 50～500nm and 2～5 μ m after second sample is cold rolled annealed, its volume ratio is about 2: 1, also has the carbide particle of the about 30nm of a small amount of diameter, has so obtained the tissue that bimodal ferrite grain size distributes.Measured the cold rolled annealed back draft stress-strain curve of two samples with electronic tensile machine.With the tabular tension specimen of Wire-cut Electrical Discharge Machining, length direction is parallel to rolling direction, the long 50mm of gauge length.After with abrasive paper for metallograph the stretching sample surfaces being polished smooth, carry out stretching experiment on electronic tensile machine, elongation is measured with extensometer.The tensile stress-strain curve that obtains as shown in Figure 1.The result shows that 6.1%, the second 11.3%, the second sample percentage of total elongation of first sample percentage of total elongation improves 85% than first sample; Second sample tensile strength is 615MPa, reduces by 23% than first sample (800MPa).First sample almost do not have uniform elongation, and second sample uniform elongation is 8%.
Claims (2)
1. the manufacture method of a high-plastic ultra-fine grain micro-alloy low-carbon steel is characterized in that: concrete technical process is:
A. the 14MnNb steel is heated to 950～1020 ℃ of insulation 20～40min, furnace cooling to 840～800 ℃, insulation 20～40min, then rapidly in 8～15% salt solution quench cooled to room temperature;
B. carry out room temperature multi-pass rolling deformation after, rolling total reduction is 60～80%;
C. carry out recrystallization annealing after rolling and handle, treatment process is: be heated to 500～600 ℃, soaking time is 1～2h, the air cooling of coming out of the stove.
2. the manufacture method of high-plastic ultra-fine grain micro-alloy low-carbon steel according to claim 1, it is characterized in that: the high-plastic ultra-fine grain micro-alloy low-carbon steel that uses above-mentioned technology to make, have simultaneously than high elongation rate keeping high-intensity, elongation is 11.3%, tensile strength is 615MPa, the ultrafine-grained (UFG) microstructure that obtains with recrystallization annealing behind the complete martensite deformation at room temperature compares, and improves 85% and reduce by 23% respectively.
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101974671A (en) * | 2010-11-09 | 2011-02-16 | 燕山大学 | Method for manufacturing high-strength superfine crystalline spring steel |
| CN103255273A (en) * | 2013-05-20 | 2013-08-21 | 南京钢铁股份有限公司 | Manufacturing method capable of improving plasticity of pipeline steel plate |
| CN105002440A (en) * | 2015-07-28 | 2015-10-28 | 兰州理工大学 | Preparation method of nanometer/micro-grain complex-phase high-strength high-plasticity 304 stainless steel sheet |
| CN106011422A (en) * | 2016-08-03 | 2016-10-12 | 唐山学院 | High-strength steel with bimodal scale ferrite structure and low cost preparation method thereof |
| CN108998636A (en) * | 2018-01-12 | 2018-12-14 | 燕山大学 | A kind of preparation method of work softening mild steel |
| CN114635018A (en) * | 2022-03-23 | 2022-06-17 | 安徽工业大学 | Method for enhancing and plasticizing Q345 low-carbon steel |
-
2008
- 2008-01-22 CN CNB2008100091359A patent/CN100537791C/en not_active Expired - Fee Related
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101974671A (en) * | 2010-11-09 | 2011-02-16 | 燕山大学 | Method for manufacturing high-strength superfine crystalline spring steel |
| CN103255273A (en) * | 2013-05-20 | 2013-08-21 | 南京钢铁股份有限公司 | Manufacturing method capable of improving plasticity of pipeline steel plate |
| CN105002440A (en) * | 2015-07-28 | 2015-10-28 | 兰州理工大学 | Preparation method of nanometer/micro-grain complex-phase high-strength high-plasticity 304 stainless steel sheet |
| CN106011422A (en) * | 2016-08-03 | 2016-10-12 | 唐山学院 | High-strength steel with bimodal scale ferrite structure and low cost preparation method thereof |
| CN108998636A (en) * | 2018-01-12 | 2018-12-14 | 燕山大学 | A kind of preparation method of work softening mild steel |
| CN108998636B (en) * | 2018-01-12 | 2020-03-31 | 燕山大学 | Preparation method of processing softened low-carbon steel |
| CN114635018A (en) * | 2022-03-23 | 2022-06-17 | 安徽工业大学 | Method for enhancing and plasticizing Q345 low-carbon steel |
| CN114635018B (en) * | 2022-03-23 | 2024-01-26 | 安徽工业大学 | Method for reinforcing and plasticizing Q345 low-carbon steel |
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| CN100537791C (en) | 2009-09-09 |
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