CN102719736A - Steel with yield ratio of 0.9 or more used for ultra-fine grain slideway and production method thereof - Google Patents
Steel with yield ratio of 0.9 or more used for ultra-fine grain slideway and production method thereof Download PDFInfo
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- CN102719736A CN102719736A CN2012101911648A CN201210191164A CN102719736A CN 102719736 A CN102719736 A CN 102719736A CN 2012101911648 A CN2012101911648 A CN 2012101911648A CN 201210191164 A CN201210191164 A CN 201210191164A CN 102719736 A CN102719736 A CN 102719736A
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Abstract
The invention relates to a steel with the yield ratio of 0.9 or more used for an ultra-fine grain slideway and a production method thereof. The steel mainly comprises the following components in percentage by weight: 0.03-0.07% of C, less than or equal to 0.03% of Si, 0.50-0.80% of Mn, 0.02-0.07% of Al, less than or equal to 0.03% of P, less than or equal to 0.015% of S, 0.02-0.07% of Nb, less than or equal to 0.06% of Mo and the balance of Fe and impurities. The production steps comprise hot metal desulphurization, converter smelting, ladle argon blowing, continuous casting, casting blank heating, hot rolling, reeling, ordinary scouring, cold rolling, continuous annealing, and leveling for stand-by. The defects that the existing same-level high-strength steel is low in yield and the specification and the welding of hot rolling materials are difficult to meet are overcome. The yield ratio of the steel disclosed by the invention achieves 0.9 or more, the grain size of the steel achieves 13 or more, and a steel plate has high yield ratio, appropriate elongation and good spot welding property.
Description
Technical field
The present invention relates to ferrous materials and working method thereof; Belong to the method for a kind of superfine crystal particle slideway with steel and production thereof; More properly be suitable for ys more than 700MPa, yield tensile ratio >=0.9 be used for automotive seat slideway or slide rail ultra-fine grained cold rolling steel and working method thereof.
Background technology
The used cold rolling steel of automotive seat slideway or slide rail require to have high-yield strength, and have certain plasticity and good weldableness, and the solution strengthening steel is guaranteeing the high-intensity while, and its carbon equivalent significantly improves, and weldableness is difficult to meet the demands.At present, auto enterprises manufacturing chair slide or sliding rail steel mainly are to rely on to produce from external imported raw material.
Through retrieval, Chinese patent number be " a kind of method of manufacture of low-carbon (LC) 700MPa grade composite strengthening ultrafine grain belt steel " patent documentation of ZL200510047632.4, and it discloses chemical composition and weight percent content (wt%) is C:0.06 ~ 0.10; Si≤0.1, Mn:1.60 ~ 2.20, P＜0.01; S＜0.01, Nb:0.05 ~ 0.07, V:0.05 ~ 0.07; Ti:0.05 ~ 0.07; All the other are Fe, and it belongs to hot-rolled steel sheet (finished product thickness 3 ~ 8mm), and slideway or sliding rail steel required thickness are at the cold rolled annealed steel of 1.4 ~ 1.6mm.As adopt HRS can't reach this thickness requirement, simultaneously, surface quality also is difficult to reach requirement.This documents steel is to adopt Nb, V, Ti microalloying, and content is all very high, and Mn content is also very high in addition, causes weldableness not meet the demands.This documents steel microtexture is ferritic+bainite, and the forming property of this kind weave construction is not enough.
Summary of the invention
The invention reside in and overcome above-mentioned deficiency, provide a kind of process energy consumption low, stable mechanical property; And satisfying under the prerequisite that ys is not less than 700MPa, require yield tensile ratio >=0.9, unit elongation is not less than 15%; Crooked 180 ° of wide cold bending test, flexual center diameter d=0 is in the metallographic structure; Deng an axle ferritic volume percent content is 80～84%, and the granular pearlite volume percent content is that the superfine crystal particle slideway of 16～20% yield tensile ratio >=0.9 is with steel and working method thereof.
Realize the measure of above-mentioned purpose:
The superfine crystal particle slideway of a kind of yield tensile ratio>=0.9 is used steel, and its main ingredient and weight percent content are: C:0.03～0.07%, Si≤0.03%; Mn:0.50～0.80%, Al:0.02～0.07%, P≤0.03%; S≤0.015%; Nb:0.02～0.07%, Mo≤0.06%, all the other are Fe and unavoidable impurities; Mechanical property: yield tensile ratio>=0.9, unit elongation is not less than 15%, crooked 180 ° of wide cold bending test; Flexual center diameter d=0, in the metallographic structure, waiting a ferritic volume percent content is 80～84%; The granular pearlite volume percent content is 16～20%, and grain size number is not less than 13 grades.
It is characterized in that: also be added with Cr≤0.07% or Cu≤0.05% or Ni≤0.06% or wherein two kinds and above element.
Produce the method for the superfine crystal particle slideway of a kind of yield tensile ratio >=0.9, its step with steel:
1) carries out desulfurizing iron, S≤0.005% in the control molten iron;
2) converter smelting;
3) carry out ladle argon-blown, argon blowing time is 5～10 minutes, and the argon flow is 6 ~ 7 cubic decimeters/second;
4) carry out continuous casting, carry out argon envelope protection cast, the control teeming temperature is at 1540～1550 ℃;
5) to the strand heating, heating and temperature control is at 1200～1250 ℃;
6) carry out hot rolling, conventional roughing, the control finishing temperature is at 900～920 ℃;
7) batch, coiling temperature is controlled at 610～650 ℃;
8) carry out conventional pickling;
9) carry out cold rollingly, control total draft 69～71%;
10) carry out continuous annealing: control preheating temperature at 770～820 ℃, and carry out the routine insulation; Under 30～35 ℃/second speed of cooling, be cooled to 350～450 ℃, and carry out being cooled to room temperature again after 120～150 seconds the timeliness;
11) carry out smooth, and for use.
The effect of each element and master operation and mechanism among the present invention
C is cheap, and simultaneously, C also is the solution strengthening element, and strengthening effect is fairly obvious, and C content is high more good more to strengthening effect.But the C too high levels is unfavorable for guaranteeing material welding performance.Therefore, C content is controlled at 0.03 ~ 0.07%.
The Si element solid solution improve the intensity of steel, but the C too high levels is unfavorable for guaranteeing material welding performance in ferritic.Therefore, the upper limit content of Si element of the present invention in steel is controlled at below 0.03%.
The Mn element is conventional highly malleablized element, as austenite former, enlarging the austenitic area, reduces finishing temperature, postpones austenitic transformation, can play the effect of crystal grain thinning simultaneously.But the Mn constituent content is too high, increases the hardening capacity of steel, makes weld structure hardened layer occur and causes crackle weld seam and heat-affected zone crack susceptibility to increase.Therefore, Mn content is controlled at 0.50 ~ 0.80%.
Al in the present invention, main effect is deoxidation in steelmaking process, makes molten steel calm.Simultaneously, (N C) separates out, and plays the intensity effect that improves steel in Finished Steel, to have Al.Therefore the Al lower limit is controlled at 0.02%, and the upper limit is controlled at 0.07%.
P is prone to increase the cold shortness of steel, and unfavorable to plasticity, weldableness and plasticity simultaneously, therefore, P content is controlled at below 0.030%.
S is unfavorable to the plasticity and toughness of material of the present invention, reduces erosion resistance, and simultaneously, for avoiding producing the strand crackle, therefore restriction S content, require S≤0.015%.
Nb is a kind of strong carbonitride forming element, helps precipitation strength, and can stop high temperature austenite too to be grown up, and has extremely strong crystal grain thinning effect.But the Nb too high levels causes carbonitride to gather partially easily, and its processibility variation simultaneously, has increased material cost.Therefore, Nb content is controlled at 0.02 ~ 0.07%.
Cr, Ni, Mo, Cu significantly improve ys, and increase erosion resistance.
The present invention also brings up to 900～920 ℃ to finishing temperature, and rolling to obtain uniform grain-size to guarantee steel plate austenite one phase district, temperature is too high; Grain-size is thick; Intensity is difficult to reach requirement, and temperature is low excessively, because of alloying element more; Mixed crystal phenomenon can take place, and causes mechanical property undesirable.
Product of the present invention has solved low problem of existing same level high-strength steel such as dual phase steel and TRIP steel surrender or hot rolling material specification and has welded the problem that is difficult to meet the demands.Since its yield tensile ratio reach 0.9 and more than, thereby guaranteed the shape stability that material uses; Realized refined crystalline strengthening, and grain fineness number is reached more than 13 grades, steel plate has high-yield-ratio and moderate elongation and good spot weldability, has embodied to have better market prospect and remarkable social benefit and economic benefit.
Description of drawings
Accompanying drawing amplifies 500 times of observations for steel plate of the present invention through metallographic, for waiting metallographic structure of axle ferritic+granular pearlite.
Embodiment
Describe in detail in the face of the present invention down:
Table 1 is the chemical composition and the weight percent content tabulation of various embodiments of the present invention and Comparative Examples.
Table 2 is the main technologic parameters tabulation of various embodiments of the present invention and Comparative Examples, and it carries out according to following process step:
1) carries out desulfurizing iron, S≤0.005% in the control molten iron;
2) converter smelting;
3) carry out ladle argon-blown, argon blowing time is 5～10 minutes, and the argon flow is 6 ~ 7 cubic decimeters/second;
4) carry out continuous casting, carry out argon envelope protection cast, the control teeming temperature is at 1540～1550 ℃;
5) to the strand heating, heating and temperature control is at 1200～1250 ℃;
6) carry out hot rolling, conventional roughing, the control finishing temperature is at 900～920 ℃;
7) batch, coiling temperature is controlled at 610～650 ℃;
8) carry out conventional pickling;
9) carry out cold rollingly, control total draft 69～71%;
10) carry out continuous annealing: control preheating temperature at 770～820 ℃, and carry out the routine insulation; Under 30～35 ℃/second speed of cooling, be cooled to 350～450 ℃, and carry out being cooled to room temperature again after 120～150 seconds the timeliness;
11) carry out smooth, and for use.
Table 3 is the mechanical property and the tabulation of metallographic structure detected result of various embodiments of the present invention and Comparative Examples.
The component of table 1 various embodiments of the present invention and Comparative Examples and the tabulation of wt% content
| Embodiment | C | Si | Mn | P | S | Al | Nb | Cr | Cu | Ni | Mo | V | Ti |
| 1 | 0.03 | 0.01 | 0.80 | 0.010 | 0.008 | 0.04 | 0.05 | / | / | / | 0.03 | / | / |
| 2 | 0.05 | 0.01 | 0.60 | 0.010 | 0.008 | 0.04 | 0.04 | 0.03 | / | / | 0.05 | / | / |
| 3 | 0.07 | 0.01 | 0.50 | 0.010 | 0.008 | 0.04 | 0.02 | / | 0.04 | / | 0.06 | / | / |
| 4 | 0.07 | 0.01 | 0.50 | 0.010 | 0.008 | 0.04 | 0.03 | / | 0.04 | / | 0.02 | / | / |
| 5 | 0.05 | 0.01 | 0.60 | 0.010 | 0.008 | 0.04 | 0.04 | 0.03 | 0.04 | / | 0.05 | / | / |
| 6 | 0.03 | 0.01 | 0.80 | 0.010 | 0.008 | 0.04 | 0.07 | / | / | 0.05 | 0.03 | / | / |
| 7 | 0.06 | 0.01 | 0.55 | 0.009 | 0.010 | 0.05 | 0.06 | 0.07 | 0.05 | / | 0.04 | / | / |
| 8 | 0.04 | 0.01 | 0.62 | 0.012 | 0.006 | 0.038 | 0.05 | / | 0.03 | 0.02 | 0.03 | / | / |
| 9 | 0.06 | 0.02 | 0.04 | 0.013 | 0.006 | 0.045 | 0.05 | / | / | 0.06 | 0.04 | / | / |
| Contrast 1 | 0.06 | 0.10 | 2.20 | 0.003 | 0.008 | / | 0.05 | / | / | / | / | 0.07 | 0.07 |
| Contrast 2 | 0.10 | 0.07 | 1.60 | 0.007 | 0.005 | / | 0.06 | / | / | / | / | 0.07 | 0.06 |
| Contrast 3 | 0.06 | 0.08 | 1.60 | 0.003 | 0.006 | / | 0.07 | / | / | / | / | 0.05 | 0.07 |
The main technologic parameters tabulation of table 2 various embodiments of the present invention and Comparative Examples
The mechanical property of table 3 various embodiments of the present invention and Comparative Examples and the tabulation of metallographic structure detected result
Can find out that from table 3 yield tensile ratio of the present invention is higher, bending property is better, from microcosmic, can find out that the forming property of material of the present invention is more excellent.
Claims (3)
1. the superfine crystal particle slideway of yield tensile ratio>=0.9 is used steel, and its main main ingredient and weight percent content are: C:0.03～0.07%, Si≤0.03%; Mn:0.50～0.80%, Al:0.02～0.07%, P≤0.03%; S≤0.015%; Nb:0.02～0.07%, Mo≤0.06%, all the other are Fe and unavoidable impurities; Mechanical property: yield tensile ratio>=0.9, unit elongation is not less than 15%, crooked 180 ° of wide cold bending test; Flexual center diameter d=0, in the metallographic structure, waiting a ferritic volume percent content is 80～84%; The granular pearlite volume percent content is 16～20%, and grain size number is not less than 13 grades.
2. the superfine crystal particle slideway of a kind of yield tensile ratio as claimed in claim 1>=0.9 is used steel, it is characterized in that: also be added with Cr≤0.07% or Cu≤0.05% or Ni≤0.06% or wherein two kinds and above element.
3. the superfine crystal particle slideway of the described a kind of yield tensile ratio of production claim 1 >=0.9 is with the method for steel, its step:
1) carries out desulfurizing iron, S≤0.005% in the control molten iron;
2) converter smelting;
3) carry out ladle argon-blown, argon blowing time is 5～10 minutes, and the argon flow is 6 ~ 7 cubic decimeters/second;
4) carry out continuous casting, carry out argon envelope protection cast, the control teeming temperature is at 1540～1550 ℃;
5) to the strand heating, heating and temperature control is at 1200～1250 ℃;
6) carry out hot rolling, conventional roughing, the control finishing temperature is at 900～920 ℃;
7) batch, coiling temperature is controlled at 610～650 ℃;
8) carry out conventional pickling;
9) carry out cold rollingly, control total draft 69～71%;
10) carry out continuous annealing: control preheating temperature at 770～820 ℃, and carry out the routine insulation; Under 30～35 ℃/second speed of cooling, be cooled to 350～450 ℃, and carry out being cooled to room temperature again after 120～150 seconds the timeliness;
11) carry out smooth, and for use.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107164700A (en) * | 2017-05-27 | 2017-09-15 | 唐山钢铁集团有限责任公司 | A kind of 800MPa grades of high-yield-ratio cold-rolled strip and its manufacture method |
| CN109440015A (en) * | 2018-11-12 | 2019-03-08 | 包头钢铁（集团）有限责任公司 | A kind of 400MPa grades of cold rolling sliding rail steel and its manufacturing method |
| CN109988970A (en) * | 2019-04-01 | 2019-07-09 | 山东钢铁集团日照有限公司 | A kind of cold rolling Q&P980 steel and its production method with different yield tensile ratios |
| CN113201691A (en) * | 2021-04-28 | 2021-08-03 | 攀钢集团攀枝花钢铁研究院有限公司 | Hot rolled steel plate for 590 MPa-level hydraulic bulging and preparation method thereof |
| WO2022042622A1 (en) | 2020-08-27 | 2022-03-03 | 宝山钢铁股份有限公司 | Gpa-grade bainite steel having ultra-high yield ratio and manufacturing method for gpa-grade bainite steel |
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| JP2003193190A (en) * | 2001-12-28 | 2003-07-09 | Nippon Steel Corp | Galvanized high strength steel sheet having excellent weldability, hole expansibility and corrosion resistance and production method therefor |
| JP2009179851A (en) * | 2008-01-31 | 2009-08-13 | Jfe Steel Corp | Method for producing cold-rolled steel sheet |
| CN102395695A (en) * | 2009-04-13 | 2012-03-28 | 杰富意钢铁株式会社 | Cold-rolled steel sheet having excellent slow-aging property and high curability in baking, and method for producing same |
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- 2012-06-12 CN CN201210191164.8A patent/CN102719736B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2003193190A (en) * | 2001-12-28 | 2003-07-09 | Nippon Steel Corp | Galvanized high strength steel sheet having excellent weldability, hole expansibility and corrosion resistance and production method therefor |
| JP2009179851A (en) * | 2008-01-31 | 2009-08-13 | Jfe Steel Corp | Method for producing cold-rolled steel sheet |
| CN102395695A (en) * | 2009-04-13 | 2012-03-28 | 杰富意钢铁株式会社 | Cold-rolled steel sheet having excellent slow-aging property and high curability in baking, and method for producing same |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107164700A (en) * | 2017-05-27 | 2017-09-15 | 唐山钢铁集团有限责任公司 | A kind of 800MPa grades of high-yield-ratio cold-rolled strip and its manufacture method |
| CN107164700B (en) * | 2017-05-27 | 2018-11-09 | 唐山钢铁集团有限责任公司 | A kind of 800MPa grades of high-yield-ratio cold-rolled strip and its manufacturing method |
| CN109440015A (en) * | 2018-11-12 | 2019-03-08 | 包头钢铁（集团）有限责任公司 | A kind of 400MPa grades of cold rolling sliding rail steel and its manufacturing method |
| CN109988970A (en) * | 2019-04-01 | 2019-07-09 | 山东钢铁集团日照有限公司 | A kind of cold rolling Q&P980 steel and its production method with different yield tensile ratios |
| WO2022042622A1 (en) | 2020-08-27 | 2022-03-03 | 宝山钢铁股份有限公司 | Gpa-grade bainite steel having ultra-high yield ratio and manufacturing method for gpa-grade bainite steel |
| CN113201691A (en) * | 2021-04-28 | 2021-08-03 | 攀钢集团攀枝花钢铁研究院有限公司 | Hot rolled steel plate for 590 MPa-level hydraulic bulging and preparation method thereof |
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