CN107326282B - 600MPa grades of high-yield-ratio hot rolling high-strength light steel and its manufacturing method - Google Patents
600MPa grades of high-yield-ratio hot rolling high-strength light steel and its manufacturing method Download PDFInfo
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- CN107326282B CN107326282B CN201710570198.0A CN201710570198A CN107326282B CN 107326282 B CN107326282 B CN 107326282B CN 201710570198 A CN201710570198 A CN 201710570198A CN 107326282 B CN107326282 B CN 107326282B
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- 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
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Abstract
The present invention provides a kind of 600MPa grades of high-yield-ratio hot rolling high-strength light steel, its chemical composition is by mass percentage：C:0.05%~0.20%, Mn:0.50%~2.00%, Si:0.05~0.50%；Al:3.0~8.0%, Nb:0.02~0.10%, P≤0.015%, S≤0.010%, N≤0.008%, Ca:0.0001 0.10%, remaining is Fe and inevitable impurity.The present invention is controlled by the combination of ingredient and technique, the high-tensile, high-yield-ratio, outstanding cold-bending property of lightweight steel may be implemented, and density is reduced, and it is also relatively easy to smelting, the control of the operation of rolling, the control of production efficiency and process cost is greatly improved.
Description
Technical field
The present invention relates to lightweight steel making field, in particular to a kind of 600MPa grades of high-yield-ratio hot rolling high-strength light steel and
Its manufacturing method.
Background technology
In recent years, with the propulsion of energy-saving and emission-reduction technology of vehicles, automotive light weight technology becomes a kind of development trend.Automotive material
Lightweight generally use two ways realizes, a kind of method be the dosage of steel is reduced by using Thin Specs high-strength steel, and
Another method is then to reduce the weight of steel by reducing the density of steel, to reduce the dosage of steel.At second
In method, since Al alloys have the characteristics that density is small, atomic radius is big, Al becomes the crucial alloy for reducing density, is
So that steel density is reduced by 4% or more, 3% or more Al can be added in general steel.Simultaneously in order to improve the plasticity of steel, make steel
In contain certain retained austenite, so that steel is generated TRIP TWIP effects in deformation process, in steel also added with compared with
The alloying elements such as more Mn, Ni.Therefore generally there are following problems in the prior art：On the one hand, the alloying elements such as a large amount of Mn, Ni
Addition cause this kind of low density steel to be rolled in delta ferrite and γ austenite two-phase sections always, cause the banded structure of steel tight
Again, the problems such as and then making material generate anisotropic, easy to produce cold bend cracking.In order to mitigate banded structure, this kind of product is logical
The cold rolling and annealing using multi-pass are often needed, but effect is still undesirable.On the other hand, the yield tensile ratio of this kind of steel usually compared with
It is low, generally below 0.80, the purposes of high-yield-ratio cannot be met.
In addition, in the method for realizing steel low-density, also there is the Al by addition 6~9%, and reduce the carbon in steel
It is extremely PPm grades several, and a small amount of Mn is added, the product of 0.5~2.0mm of thickness, but its are produced by the way of cold rolling, annealing
Tensile strength 550MPa hereinafter, yield tensile ratio below 0.80.
Invention content
The object of the present invention is to provide a kind of 600MPa grades of high-yield-ratio hot rolling high-strength light steel, its not only light weight, and
And tensile strength is high, yield tensile ratio is high.
To achieve the above object, the present invention provides a kind of 600MPa grades of high-yield-ratio hot rolling high-strength light steel, its chemistry
Ingredient is by mass percentage：C:0.05%~0.20%, Mn:0.50%~2.00%, Si:0.05~0.50%；Al:
3.0~8.0%, Nb:0.02~0.10%, P≤0.015%, S≤0.010%, N≤0.008%, Ca:0.0001~
0.10%, remaining is Fe and inevitable impurity.
Also, the mass percent of C, Al, Mn, Nb in the lightweight steel meet 0.10≤(15C+0.5Mn)/(Al+
10Nb)≤0.40, Mn/Al≤0.25.
The effect of each element and main technique and mechanism in the present invention：
C：Carbon plays solution strengthening effect in steel, or forms MC fine particles with carbide formers such as Nb in steel,
Play the role of precipitation strength and crystal grain thinning, improves the intensity of steel.But carbon content is excessively high to be easy to be formed excessively in steel
Pearlite reduces the yield tensile ratio of steel, and then reduces the toughness of steel, and carbon content is excessively high, and banded structure is easily formed in steel,
The processability and welding performance for leading to steel decline, therefore the C content in the present invention is selected as 0.05%~0.20%, more excellent
It is selected as 0.05~0.15%.
Mn：Mn plays solution strengthening and stable austenite in steel, is conducive to the yield tensile ratio for improving steel.Content mistake
Low, invigoration effect is too small.Mn too high levels are easy to cause austenite content in steel and increase, to increase steel medium pearlite etc. second
The ratio of phase constitution is unfavorable for obtaining ferritic structure.In addition, Mn too high levels are also easy to cause in steel and form banded structure,
Material is caused to be easy cracking in Cold Roll Forming Process, therefore Mn contents of the present invention are 0.50~2.00%.
Al：Al is lightweight element, since its atomic mass is small and bigger than iron atom radius, can effectively reduce the close of steel
Degree, therefore be the main adding elements of lightweight steel, Al is also ferrite former, promotes ferritic formation in steel.But Al
The excessively high compound between forming FeAl of constituent content reduces steel toughness.Therefore Al content is 3.0~8.0% in the present invention, more
Preferably 4.0~6.5%.
Si：Si plays solution strengthening effect in steel, and Si contents are too low, solid solution strengthening effect unobvious, but Si too high levels
Surface Quality has an adverse effect, therefore Si contents of the present invention are 0.05~0.50%.
Nb：Nb plays solution strengthening effect in steel, is combined to form NbC and NbN with C, N in steel, plays precipitation strength
Effect, and Nb is strong ferrite former, is conducive to form ferritic structure in steel, but Nb too high levels can increase and roll
Load processed makes rolling be difficult to carry out, and Nb is precious metal, and Nb too high levels can greatly increase the manufacturing cost of steel, therefore
The content of Nb is 0.02~0.10% in the present invention.
C, Al, Mn, Nb constituent content need to meet 0.10≤(15C+0.5Mn)/(Al+10Nb)≤0.40, Mn/ in the present invention
Al≤0.25.As 0.10≤(15C+0.5Mn)/(Al+10Nb)≤0.40, Mn/Al≤0.25, it is ensured that the ferrite in steel
Tissue >=99%, ensures the intensity and toughness of steel, and can effectively improve the welding performance of steel.Preferably 0.15≤(15C+
0.5Mn)/(Al+10Nb)≤0.40。
P：P is the impurity element in steel, is easy to influence the toughness of product in crystal boundary segregation, therefore the lower its content the better.
According to practical controlled level, should control below 0.015%.
S：S is the impurity element in steel, easily generates segregation in crystal boundary, and form the FeS of low melting point with the Fe in steel, reduces
The toughness of steel, when steel-making, should fully remove, and should control within 0.010%.
N：N is the impurity element in steel, reduces the toughness of steel, is easy to form AlN and NbN, content mistake with Al, Nb in steel
Height easily forms coarse AlN and NbN, therefore reduces its content as possible, should control below 0.008%.
Ca：The calcium of certain content can improve the state of steel inclusion, to be conducive to improve the toughness of steel, therefore this hair
Bright middle Ca is 0.0001~0.0050%.
Another object of the present invention is the manufacturing method of above-mentioned 600MPa grades of high-yield-ratio hot rolling high-strength light steel, the party
Method step is simple, at low cost, is suitable for industrialized production.
To achieve the above object, the present invention provides a kind of manufacture of above-mentioned 600MPa grades of high-yield-ratios hot rolling high-strength light steel
Method, it includes the following steps successively：Continuous casting, heating strand, hot rolling, cooling are batched, it is characterised in that：
1) in the continuous casting stage, pulling speed of continuous casting 0.5m/min~10.0m/min, 15~30 DEG C of the degree of superheat of casting；
2) in the heating strand stage, heating of plate blank rate is 5 DEG C/min~50 DEG C/min, and slab tapping temperature is
1180~1300 DEG C, heating time is 30min~200min；
3) in the hot rolling stage, hot rolling compression ratio >=90%, hot rolling finishing temperature is 860~950 DEG C；
4) in the cooling coil ing one, strip cooling rate >=20 DEG C/s, coiling temperature is 580~680 DEG C.
Preferably, it uses slab CC machine, heavy slab first to cool down in the step 1), strand is carried out subsequently into heating furnace
It heats, in heavy slab elder generation cooling procedure, cooling rate≤50 DEG C/min, when the entrance heating furnace carries out heating strand,
Slab charging temperature >=200 DEG C, the rate of heat addition≤20 DEG C/min.
It is furthermore preferred that heavy slab described in the step 1) carries out slow cooling using insulation cover.
Preferably, slab tapping temperature is 1200~1250 DEG C in the step 2).
Preferably, hot rolling finishing temperature is 860~920 DEG C in the step 3).
Preferably, ferrite volume fraction is not less than 99% in the band structure of steel in the step 3) after hot rolling.
Preferably, strip cooling rate >=30 DEG C/s in the step 4).
Preferably, the type of cooling of strip includes in cooling leading portion, two sections of coolings and multistage cooling in the step 4)
It is one or more of.More preferably using the type of cooling of leading portion cooling.
It is using the reasons why above-mentioned technique：
When the continuous casting stage, casting speed control can effectively subtract in 0.5m/min~10.0m/min, degree of superheat control at 15~30 DEG C
Few center segregation of casting blank, loose and slab surface crack generation,
In the heating strand stage, the coefficient of thermal expansion of steel is improved since a large amount of Al being added in steel, and rate mistake is added
Height easily causes continuous casting billet and generates cracking because internal stress is excessive, and addition rate is too low, and heating time is long, causes surface de-
Carbon is serious, and coarse grains in steel reduce the toughness of steel.Therefore the rate of heat addition of the present invention is 5~50 DEG C/min.
Meanwhile tapping temperature is at 1180~1300 DEG C in the present invention, this is because containing alloy element Nb in steel, heating is warm
When spending low, the carbonitride formed in slab cooling procedure is difficult to be dissolved, and reduces its refined crystalline strengthening and solid solution strengthening effect.In addition
Slab tapping temperature is too low, and resistance of deformation increases, it is difficult to and it rolls, and easy tos produce side and split problem, and temperature is too high be easy to cause
Decarburization is serious and coarse grains, reduction steel toughness equally lead to the problem of side and splits.
The heating time of the present invention is 30~200min, and heating time is too short, the poor temperature uniformity of slab, alloying element
Spread insufficient, and heating time is too long, and it is serious to be easy to cause steel slab surface decarburization.Therefore heating time of the invention be 30~
200min。
In hot rolling stage, 860~950 DEG C of finishing temperature of the invention, finishing temperature is excessively high, and crystal grain cannot obtain effectively thin
Change, reduce steel toughness and intensity, finishing temperature is too low, and resistance of deformation increases, and causes board rolling, and be easy to form band in steel
Shape tissue reduces the toughness of steel.
After hot rolling of the present invention in strip cooling procedure, strip cooling rate >=20 DEG C/s, 580~680 DEG C of coiling temperature.Band
Steel cooling rate is too low, forms banded structure in steel, and increase the content of steel medium pearlite, reduces toughness.Coiling temperature is excessively high,
The ferrite crystal grain formed in steel is excessively coarse, reduces the intensity and plasticity of steel, and coiling temperature is too low, and steel cannot be returned fully
The plasticity of multiple and recrystallization, steel reduces.
The beneficial effects of the present invention are：
The present invention is compared with prior art：The present invention provide a kind of 600MPa grades of high-yield-ratio hot rolling high-strength light steel and its
Manufacturing method.There is the steel of the present invention 99% or more ferrite, tensile strength to reach 600MPa or more, and elongation percentage reaches
18% or more, and yield tensile ratio is more than 0.80, density 7.50g/cm3Hereinafter, weight need not be mitigated by reducing steel plate thickness,
Steel plate thickness is up to 1.0~10.0mm.The hot-rolled product of the present invention is high with intensity, plasticity is good, cold-bending property is good, density is low
The features such as, density ratio conventional variety reduces by 5% or more, has good loss of weight potentiality, is suitable for automobile structure and reinforcer
Manufacture.Since the microstructure that the present invention obtains is pure ferritic structure, banded structure existing in the prior art is overcome,
Improve properties of product uniformity and cold-bending property.This manufacturing method is simple and practicable, is not necessarily to additional equipment investment, is suitable for
Industrialized production has very strong practicability.
Specific implementation mode
The 600MPa grade high-yield-ratio hot rolling high-strength light steel to the present invention and its manufacturer below by way of specific embodiment
Method is further described：
Table 1 list 1~embodiment of embodiment 5 of serial number 1~5 600MPa grade high-yield-ratio hot rolling high-strength light steel and
The lightweight steel chemical composition of 1~comparative example of comparative example 3 of serial number 6~8 weight percent (surplus be Fe and inevitably it is miscellaneous
Matter).
The chemical composition (wt, %) of 1 embodiment of table
The 600MPa grade high-yield-ratio hot rolling high-strength light steel and sequence of 1~embodiment of embodiment 5 of serial number 1~5 of the present invention
The lightweight steel of numbers 6~8 1~comparative example of comparative example 3 manufactures as follows to be obtained, and specific process parameter is as shown in table 2：
It includes the following steps successively：Continuous casting, heating strand, hot rolling, cooling are batched, it is characterised in that：
1) in the continuous casting stage, pulling speed of continuous casting 0.5m/min~10.0m/min, 15~30 DEG C of the degree of superheat of casting；
2) in the heating strand stage, heating of plate blank rate is 5 DEG C/min~50 DEG C/min, and slab tapping temperature is
1180~1300 DEG C, heating time is 30min~200min；
3) in the hot rolling stage, hot rolling compression ratio >=90%, hot rolling finishing temperature is 860~950 DEG C；
4) in the cooling coil ing one, strip cooling rate >=20 DEG C/s, coiling temperature is 580~680 DEG C.
The manufacturing approach craft parameter of 2 each embodiment of table
| Serial number | Slab tapping temperature DEG C | Slab heating time min | Finishing temperature DEG C | Cooling rate DEG C/s | Coiling temperature DEG C |
| 1 | 1180 | 30 | 890 | 60 | 620 |
| 2 | 1200 | 180 | 920 | 30 | 650 |
| 3 | 1250 | 160 | 935 | 27 | 600 |
| 4 | 1300 | 200 | 950 | 35 | 680 |
| 5 | 1230 | 150 | 900 | 56 | 580 |
| 6 | 1190 | 180 | 870 | 40 | 620 |
| 7 | 1230 | 180 | 880 | 45 | 630 |
| 8 | 1230 | 160 | 890 | 30 | 620 |
By the 600MPa grade high-yield-ratio hot rolling high-strength light steel and serial number 6 of 1~embodiment of embodiment 5 of serial number 1~5~
The lightweight steel of 8 1~comparative example of comparative example 3 carries out performance detection, and main performance testing result is as shown in table 3.
3 each embodiment main performance testing result of table
From table 3 it is observed that product of the present invention is organized as ferritic structure, tensile strength reaches 600MPa or more,
Elongation percentage is more than 18%, and yield tensile ratio is higher than 0.80, and without banded structure in tissue, cold-bending property is good, density 7.50g/cm3With
Under, density ratio routine steel grade (7.85g/cm3) 5.0% or more is reduced, and the chemical composition of the comparative example of serial number 4 and 5 does not exist
The scope of the present invention, although its tensile strength reaches 600MPa or more, yield tensile ratio is less than 0.80, and elongation percentage is less than 18%, and
There is banded structure in product, and the cold-bending property of product is unqualified.The comparative example of serial number 6 is less than due to C, Mn content in steel
The lower limit of the present invention, leads to its final low cross-intensity, is unsatisfactory for the requirement of tensile strength 600MPa or more of the present invention.
The scientific research personnel of technical field can according to the above-mentioned change for making content and form unsubstantiality without departing from
Institute's essential scope of the present invention, therefore, the present invention is not limited to above-mentioned specific embodiment.
Claims (9)
1. a kind of 600MPa grades of high-yield-ratio hot rolling high-strength light steel, it is characterised in that：Its chemical composition is by weight percent
It is calculated as：C:0.05%~0.20%, Mn:0.50%~2.00%, Si:0.05~0.50%；Al:3.0~8.0%, Nb:0.02
~0.10%, P≤0.015%, S≤0.010%, N≤0.008%, Ca:0.0001-0.0050%, remaining is Fe and can not keep away
The impurity exempted from；
Mass percent satisfaction 0.10≤(15C+0.5Mn)/(Al+10Nb) of C, Al, Mn, Nb in the wherein described lightweight steel≤
0.40, Mn/Al≤0.25.
2. a kind of method of 600MPa grades of high-yield-ratio hot rolling high-strength light steel described in manufacturing claims 1, it include successively with
Lower step：Continuous casting, heating strand, hot rolling, cooling are batched, it is characterised in that：
1) in the continuous casting stage, pulling speed of continuous casting 0.5m/min~10.0m/min, 15~30 DEG C of the degree of superheat of casting；
2) in the heating strand stage, heating of plate blank rate be 5 DEG C/min~50 DEG C/min, slab tapping temperature be 1180~
1300 DEG C, heating time is 30min~200min；
3) in the hot rolling stage, hot rolling compression ratio >=90%, hot rolling finishing temperature is 860~950 DEG C；
4) in the cooling coil ing one, strip cooling rate >=20 DEG C/s, coiling temperature is 580~680 DEG C.
3. the manufacturing method of 600MPa grades of high-yield-ratio hot rolling high-strength light steel according to claim 2, it is characterised in that：Institute
It states and slab CC machine, heavy slab is used first to cool down in step 1), carry out heating strand subsequently into heating furnace, the heavy slab is first
In cooling procedure, cooling rate≤50 DEG C/min, when the entrance heating furnace carries out heating strand, slab charging temperature >=200
DEG C, the rate of heat addition≤20 DEG C/min.
4. the manufacturing method of 600MPa grades of high-yield-ratio hot rolling high-strength light steel according to claim 3, it is characterised in that：Institute
It states heavy slab described in step 1) and slow cooling is carried out using insulation cover.
5. the manufacturing method of 600MPa grades of high-yield-ratio hot rolling high-strength light steel according to claim 2, it is characterised in that：Institute
It is 1200~1250 DEG C to state slab tapping temperature in step 2).
6. the manufacturing method of 600MPa grades of high-yield-ratio hot rolling high-strength light steel according to claim 2, it is characterised in that：Institute
It is 860~920 DEG C to state hot rolling finishing temperature in step 3).
7. the manufacturing method of 600MPa grades of high-yield-ratio hot rolling high-strength light steel according to claim 2, it is characterised in that：Institute
It states ferrite volume fraction in the band structure of steel in step 3) after hot rolling and is not less than 99%.
8. the manufacturing method of 600MPa grades of high-yield-ratio hot rolling high-strength light steel according to claim 2, it is characterised in that：Institute
State strip cooling rate >=30 DEG C/s in step 4).
9. the manufacturing method of 600MPa grades of high-yield-ratio hot rolling high-strength light steel according to claim 2, it is characterised in that：Institute
The type of cooling for stating strip in step 4) includes one or more of cooling leading portion, two sections of coolings and multistage cooling.
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2017
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1164875A (en) * | 1995-08-31 | 1997-11-12 | 川崎制铁株式会社 | Hot-rolled steel sheet and process for producing the same |
| CN103827338A (en) * | 2011-09-09 | 2014-05-28 | 塔塔钢铁荷兰科技有限责任公司 | Low density high strength steel and method for producing said steel |
| CN103484771A (en) * | 2013-10-18 | 2014-01-01 | 北京科技大学 | High-aluminum low-density medium-thickness steel plate for ocean platform and preparation method thereof |
| JP2016084506A (en) * | 2014-10-24 | 2016-05-19 | 新日鐵住金株式会社 | Hot rolled steel sheet excellent in cold workability and production method therefor |
| CN106498307A (en) * | 2016-10-26 | 2017-03-15 | 武汉钢铁股份有限公司 | The good high-strength and high ductility lightweight steel of 780MPa level cold-forming properties and its manufacture method |
| CN106811690A (en) * | 2017-01-17 | 2017-06-09 | 北京科技大学 | A kind of preparation method of low-density lightweight steel |
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