CN103540849A - Cr-containing hot-rolling double-phase steel and production method thereof - Google Patents
Cr-containing hot-rolling double-phase steel and production method thereof Download PDFInfo
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Abstract
The invention discloses Cr-containing hot-rolling double-phase steel with chemical components of, by mass: 0.06-0.12wt% of C; 0.40-0.60% of Cr; 0.02-0.20% of Si; no more than 1.20wt% of Mn; no more than 0.015wt% of P; no more than 0.008wt% of S; 0.02-0.06wt% of Al; no more than 0.003wt% of [O]; no more than 0.005wt% of [N]; and balance of iron and inevitable trace impurities. According to the Cr-containing hot-rolling double-phase steel and the production method thereof, chemical component ratio is effectively controlled, no precious alloy element is added, and a Cr-containing component system is subjected to low-temperature coiling, such that the produced hot-rolling double-phase steel has both low cost and excellent processing and forming performance. Also, the low Si system ensures surface quality, such that application requirements of users are satisfied.
Description
Technical field
The present invention relates to smelting iron and steel technical field, particularly a kind of containing Cr hot-rolled dual-phase steel and production method thereof.
Background technology
HSLA steel has significantly improved the intensity of steel, but be conventionally accompanied by plasticity, worsens, and forming property is poor.For coordinating intensity, coordinate with plasticity, introduce composite Materials Design theory, developed dual phase steel, due to advantages such as its low yield strength ratio, high preliminary work hardening rate, good intensity and ductility cooperations, become the good novel high-strength Punching Steel of plasticity, be widely used in automotive industry.In recent years, along with automobile is to energy-conservation, loss of weight and security future development, hot-rolled dual-phase steel, with its high strength and high formability energy, has been widely used in manufacturing the members such as automotive wheel, stiffening plate, chassis, collision bumper, the various frameworks of car body.American-European and Japan has all succeeded in developing hot-rolled dual-phase steel product at present.
Hot-rolled dual-phase steel is mainly divided into that low temperature batches type and middle warm rolling is got type two classes.Low temperature batches type hot-rolled dual-phase steel be after finish to gauge and batch before complete the transformation of main iron-clad horses tissue, its coiling temperature is conventionally below 300 ℃, avoid bainite to form, also ferritic timeliness and martensitic self-tempering have been avoided simultaneously, this kind of hot-rolled dual-phase steel alloy content is relatively less, cost of alloy economy, but hot rolling technology window control is strict; It is to rely on stable austenite element to batch without phase transformation limited proportionality as Cr, Mo etc. is controlled at austenite metastable state by coil of strip that middle warm rolling is got type hot-rolled dual-phase steel, this interval is generally 500～600 ℃, after batching at air cooling to room temperature process, Transformation of Retained Austenite becomes martensite, the final iron-clad horses tissue that obtains, be easy to realize target temperature and control, but this kind of hot-rolled dual-phase steel cost of alloy is high.
The principal feature of dual phase steel in chemical composition is low-carbon and low-alloy.Main alloy element be take Si, Mn as main, different according to production technique and service requirements in addition, also can add appropriate Cr, Mo, V, Nb element, having formed with C-Si-Mn system, C-Mn-Mo system, C-Si-Mn-Cr-V system and C-Si-Mn-Cr-Mo is main dual phase steel composition series.North America hot-rolled dual-phase steel feature is to add the alloying elements such as Cr, Mo, V or Nb, and cost of alloy is higher, and comparing with HSLA does not have advantage; Japan's hot-rolled dual-phase steel feature is to be main with Si, but Si content is higher, can affect surface quality.
Summary of the invention
Technical problem to be solved by this invention is to provide that a kind of production cost economy, processability are good, free of surface defects is containing Cr hot-rolled dual-phase steel and production method thereof.
For solving the problems of the technologies described above, according to one aspect of the invention, provide a kind of containing Cr hot-rolled dual-phase steel, its chemical composition mass percent is: C:0.06～0.12wt%; Cr:0.40～0.60%; Si:0.02～0.20%; Mn :≤1.20wt%; P :≤0.015wt%; S :≤0.008wt%; Al:0.02～0.06wt%; [O] :≤0.003wt%; [N] :≤0.005wt%; Other is iron and inevitable trace impurity.
According to another aspect of the present invention, provide a kind of method of producing above-mentioned dual phase steel, comprising:
After being heated by process furnace, slab carries out soaking;
Slab after described soaking is carried out to roughing, finish rolling acquisition hot-rolled sheet;
Described hot-rolled sheet is carried out after cooling batching acquisition finished product, and coiling temperature is controlled at below 200 ℃.
Further, described while carrying out soaking after slab is heated by process furnace, Heating temperature is 1220～1280 ℃, and soaking time is 20～40 minutes, and tapping temperature is controlled at 1200～1280 ℃.
Further, it is 980～1080 ℃ that described roughing final temperature is controlled, and it is 780～900 ℃ that finish rolling final temperature is controlled, and finish rolling total deformation is greater than 80%.
Further, adopt constant speed rolling when roughing, finish rolling, hot-rolled sheet thickness specification variation range is controlled at 2～5mm, and roll speed, because of variation in thickness, is controlled at 5～10m/s.
Further, described hot-rolled sheet is carried out when cooling, first the hot-rolled sheet after finish rolling is carried out fast coolingly, cooling target temperature is 670～730 ℃, and then carries out the air cooling of 5～10s, finally carries out water-cooled again.
Provided by the invention a kind of containing Cr hot-rolled dual-phase steel and production method thereof, by effective control chemical composition proportioning, do not add precious alloy element, to adopting low temperature to batch containing Cr composition system, what guaranteed to produce is not only with low cost but also have a good machine-shaping property containing Cr hot-rolled dual-phase steel, low Si system has guaranteed surface quality simultaneously, meets user's service requirements.
Accompanying drawing explanation
Fig. 1 is the metallograph of the hot-rolled dual-phase steel produced of the embodiment of the present invention 1 after LEPRA reagent corrodes.
Fig. 2 is the metallograph of the hot-rolled dual-phase steel produced of the embodiment of the present invention 3 after LEPRA reagent corrodes.
Embodiment
The invention provides a kind of Cr hot-rolled dual-phase steel that contains, its chemical composition mass percent is: C:0.06～0.12wt%; Cr:0.40～0.60%; Si:0.02～0.20%; Mn :≤1.20wt%; P :≤0.015wt%; S :≤0.008wt%; Al:0.02～0.06wt%; [O] :≤0.003wt%; [N] :≤0.005wt%; Other is iron and inevitable trace impurity.
In Composition Design of the present invention, interpolation quantity and the strengthening mechanism of principal element is as follows:
In hot-rolled dual-phase steel, the strengthening effect of C is all influential to martensite percent by volume and martensite hardness two aspects, along with the increase of C content, can obtain more a high proportion of martensite percent by volume, but full unit elongation can corresponding reduction.For obtaining the target martensite content of 10% left and right, the C content of the embodiment of the present invention is controlled at 0.06～0.12wt%.
Mn is typical austenite stabilizer element, can improve the hardening capacity of steel, and play certain solution strengthening effect, Mn is as the element that expands γ phase region, can reduce A3, A1 stagnation point, can postpone perlitic transformation and reduce bainite transformation temperature, but also postpone simultaneously and extend ferritic transformation, Bainite Region is moved to right, thereby steel grade is slightly reduced the susceptibility of cooling control technology condition.In high Mn content Yi duplex structure, cause strengthening phase zonal arrangement.Mn content of the present invention is controlled at below 1.20wt%, has realized on the one hand lower cost of alloy and has controlled, and has guaranteed that on the other hand product has desirable tissue and good performance.
Si is non-carbide forming element, there is higher solid solution strengthening effect, can promote C to austenite enrichment, solid solution C in ferrite is had to " removing " and " purification " effect, can suppress the generation of thick carbide in process of cooling ferrite matrix, thereby improve the plasticity of dual phase steel, but with the existence of elements Si in steel, in process furnace, iron scale forms FeO/Fe with being with between steel matrix
2siO
4spinel compound, combines matrix and zone of oxidation firmly, causes the incomplete of de-scaling, finally because of the continuation of FeO oxidation, forms surperficial red scale (Fe
2o
3), and Automobile Enterprises Surface Quality is had relatively high expectations, therefore the present invention does not rely on Si to obtain duplex structure, actual Si content is controlled at below 0.05wt%, reduced the interpolation of cost of alloy, the more important thing is and solved the current hot rolling surface quality problems containing Si hot-rolled dual-phase steel, spinel compound causes the incomplete problem of de-scaling.
Cr is middle carbide, can obviously improve stability and the hardening capacity of metastable austenite, increase the austenitic cold energy power of crossing, postponement ferrite and pearlite changes, and can significantly postpone bainite transformation, be conducive to the appearance in the metastable austenite district between ferritic transformation district and bainite transformation district.The content of Cr of the present invention is controlled at 0.40～0.60wt%, together improves the stability of metastable austenite with the above-mentioned Mn element of mentioning, and has guaranteed the generation of ferrite and martensite destination organization; In addition, the Cr content within the scope of this can obtain the hot-rolled dual-phase steel of low yield strength ratio, makes product have good machine-shaping property.
A kind of method of producing above-mentioned dual phase steel is provided, comprises following step:
Step S1: carry out soaking after slab is heated by process furnace, Heating temperature is 1220～1280 ℃, and soaking time is 20～40 minutes, and tapping temperature is controlled at 1200～1280 ℃.
Step S2: the slab after described soaking is carried out to roughing, finish rolling acquisition hot-rolled sheet.
It is 980～1080 ℃ that roughing final temperature is controlled, and it is 780～900 ℃ that finish rolling final temperature is controlled, and finish rolling total deformation is greater than 80%.When roughing, finish rolling, adopt constant speed rolling, hot-rolled sheet thickness specification variation range is controlled at 2～5mm, and roll speed, because of variation in thickness, is controlled at 5～10m/s.
In the operation of rolling, adopt constant speed rolling to refer to that the throwing steel speed of last group frame of finish rolling maintains certain value, this definite value changes with hot-rolled sheet variation in thickness, the pass of the two is: the thinner roll speed of thickness is faster, and this has mainly solved hot-rolled dual-phase steel entire volume stability.By constant speed rolling can realize hot-rolled sheet different positions stable phase temperature, stablize transformation time, thereby realized the stable control of entire volume tissue, and then realize the difficulties of hot-rolled dual-phase steel stability.Hot-rolled sheet thickness specification variation range of the present invention is controlled at 2～5mm, and roll speed, because of variation in thickness, is controlled at 5～10m/s.
Step S3: described hot-rolled sheet is carried out after cooling batching acquisition finished product, and coiling temperature is controlled at below 200 ℃.
Hot-rolled dual-phase steel is mainly divided into that low temperature batches type and middle warm rolling is got type two classes.Low temperature batches type hot-rolled dual-phase steel be after finish to gauge and batch before complete the transformation of main iron-clad horses tissue, its coiling temperature is conventionally below 300 ℃, avoid bainite to form, also ferritic timeliness and martensitic self-tempering have been avoided simultaneously, this kind of hot-rolled dual-phase steel alloy content is relatively less, cost of alloy economy, but hot rolling technology window control is strict; It is to rely on stable austenite element to batch without phase transformation limited proportionality as Cr, Mo etc. is controlled at austenite metastable state by coil of strip that middle warm rolling is got type hot-rolled dual-phase steel, this interval is generally 500～600 ℃, after batching at air cooling to room temperature process, Transformation of Retained Austenite becomes martensite, the final ferrito-martensite tissue that obtains, this kind of hot-rolled dual-phase steel cost of alloy is high, but be easy to realize target temperature, controls.In the embodiment of the present invention, hot-rolled dual-phase steel is that low temperature batches type, coiling temperature is controlled at below 200 ℃, this is because martensitic phase transition process is divided into Ms (martensite start) point and martensitic transformation finishing temperature, martensitic transformation finishing temperature has determined the final volume percentage ratio of martensitic phase, for guaranteeing the percent by volume of martensitic phase, coiling temperature is controlled in lower temperature range, below 200 ℃.The present invention overcomes low temperature and batches type hot-rolled dual-phase steel technology controlling and process difficult point, realizes the production that changes this economical hot-rolled dual-phase steel with technique into.
Described hot-rolled sheet is carried out when cooling, first the hot-rolled sheet after finish rolling is carried out fast coolingly, cooling target temperature is 670～730 ℃, and then carries out the air cooling of 5～10s, finally carries out water-cooled again.
The critical tissue of the hot-rolled dual-phase steel that the embodiment of the present invention provides obtains at laminar flow cooling table.According to phase change law, hot-rolled dual-phase steel carries out ferritic structure transformation in early stage, in certain temperature range, through certain hour, complete ferritic generation, afterwards for to avoid other organization types as the generation of perlite and bainite, need under higher cooling rate, be cooled to rapidly martensite to start transition temperature point, selecting three sections of cooling modes of water-cooled+air cooling+water-cooled has been above-mentioned structural transformation process.It is 670～730 ℃ that the present invention selects ferritic structural transformation temperature range, and temperature can cause ferritic transformation insufficient higher than this scope, and temperature can cause a part of pearlitic generation lower than this scope, and then affects the generation of follow-up martensitic stucture; Air cooling time of the present invention is 5～10s, and air cooling time surpasses 10s and can cause ferrite to be produced in a large number, and it is insufficient that air cooling time can cause lower than 5s that ferrite separates out, and then affects the generation ratio of ferrite and martensite two-phase structure; Finally adopt cold quenching to obtain martensitic stucture.
The hot-rolled dual-phase steel of producing by aforementioned production method is organized as ferrite and martensite, and ferrite volume parts is 85～93%, and martensite is 7～15%, yield strength R
p0.2be 355～420MPa, tensile strength Rm is 580～650MPa, and yield tensile ratio is 0.56～0.67, A
80be that 20～28%, n value is 0.15～0.17.
Provided by the invention a kind of containing Cr hot-rolled dual-phase steel and production method thereof, by effective control chemical composition proportioning, do not add precious alloy element, adopt C-Mn-Cr composition system, three sections of cooling modes that adopt water-cooled+air cooling+water-cooled, batch and constant speed rolling by low temperature, and what guaranteed to produce is not only with low cost but also have a good machine-shaping property containing Cr hot-rolled dual-phase steel, low Si system has guaranteed surface quality simultaneously, meets user's service requirements.
Below by specific embodiment, the present invention is further described.
The equipment that slab is rolled to employing is 7 frame tandem mill groups.
Embodiment 1
Slab chemical composition is designated as carbon: 0.08wt% by weight percentage; Chromium: 0.45%; Silicon: 0.03%; Manganese: 1.10wt%; Phosphorus: 0.012wt%; Sulphur: 0.004wt%; Aluminium: 0.030wt%; [O]: 0.0022wt%; [N]: 0.0042wt%; Other is iron and inevitable trace impurity.
Production technique is as follows:
(1) by thickness, be 230mm heating of plate blank, control 1240 ℃ of Heating temperatures, soaking time is 30 minutes, 1220 ℃ of tapping temperatures.
(2) steel plate target rolling thickness specifications vary is 4mm, adopts the rolling of 5.8m/s constant speedpump.
(3) slab is rolled, it is 1010 ℃ that roughing final temperature is controlled; It is 800 ℃ that finish rolling final temperature is controlled; Finish rolling total deformation 90%.
(4) after finish rolling, carry out cooling control, the target temperature of first paragraph cooling by water is 690～700 ℃, then carries out the air cooling of 8s, finally carries out water-cooled, and coiling temperature is controlled at 80 ℃.
The chemical composition of the dual phase steel of producing is carbon: 0.08wt%; Chromium: 0.45%; Silicon: 0.03%; Manganese: 1.10wt%; Phosphorus: 0.012wt%; Sulphur: 0.004wt%; Aluminium: 0.030wt%; [O]: 0.0022wt%; [N]: 0.0042wt%; Other is iron and inevitable trace impurity; Be organized as ferrite and martensite, ferrite volume parts is 90%, and martensite is 10%, yield strength R
p0.2for 365MPa, tensile strength Rm is 616MPa, and yield tensile ratio is 0.59, A
80be that 24%, n value is 0.17.
Embodiment 2
Slab chemical composition is designated as carbon: 0.08wt% by weight percentage; Chromium: 0.45%; Silicon: 0.03%; Manganese: 1.10wt%; Phosphorus: 0.012wt%; Sulphur: 0.004wt%; Aluminium: 0.030wt%; [O]: 0.0022wt%; [N]: 0.0042wt%; Other is iron and inevitable trace impurity.
Production technique is as follows:
(1) by thickness, be 230mm heating of plate blank, control 1250 ℃ of Heating temperatures, soaking time is 20 minutes, 1220 ℃ of tapping temperatures.
(2) steel plate target rolling thickness is 2.7mm, adopts the rolling of 8m/s constant speedpump.
(3) slab is rolled, it is 1040 ℃ that roughing final temperature is controlled; It is 800 ℃ that finish rolling final temperature is controlled; Finish rolling total deformation 93%.
(4) after finish rolling, carry out cooling control, the target temperature of first paragraph cooling by water is 690～700 ℃, then carries out the air cooling of 7s, finally carries out water-cooled, and coiling temperature is controlled at 80 ℃.
The chemical composition of producing steel plate is carbon: 0.08wt%; Chromium: 0.45%; Silicon: 0.08%; Manganese: 1.10wt%; Phosphorus: 0.012wt%; Sulphur: 0.004wt%; Aluminium: 0.030wt%; [O]: 0.0022wt%; [N]: 0.0042wt%; Other is iron and inevitable trace impurity; Be organized as ferrite and martensite, ferrite volume parts is 90%, and martensite is 10%, yield strength R
p0.2for 375MPa, tensile strength Rm is 598MPa, and yield tensile ratio is 0.63, A
80be that 22%, n value is 0.16.
Embodiment 3
Slab chemical composition is designated as carbon: 0.085wt% by weight percentage; Chromium: 0.50%; Silicon: 0.15%; Manganese: 1.0wt%; Phosphorus: 0.012wt%; Sulphur: 0.002wt%; Aluminium: 0.030wt%; [O]: 0.0020wt%; [N]: 0.0040wt%; Other is iron and inevitable trace impurity.
Production technique is as follows:
(1) by thickness, be 230mm heating of plate blank, control 1220 ℃ of Heating temperatures, soaking time is 30 minutes, 1220 ℃ of tapping temperatures.
(2) steel plate target rolling thickness is 4.5mm, adopts the rolling of 5.4m/s constant speedpump.
(3) slab is rolled, it is 1060 ℃ that roughing final temperature is controlled; It is 880 ℃ that finish rolling final temperature is controlled; Finish rolling total deformation 90%.
(4) after finish rolling, carry out coiling into finished product after cooling control, the target temperature of first paragraph cooling by water is 690～700 ℃, then carries out the air cooling of 8s, finally carries out water-cooled, and coiling temperature is controlled at 80 ℃.
The chemical composition of producing steel plate is carbon: 0.085wt%; Chromium: 0.50%; Silicon: 0.15%; Manganese: 1.0wt%; Phosphorus: 0.012wt%; Sulphur: 0.002wt%; Aluminium: 0.030wt%; [O]: 0.0020wt%; [N]: 0.0040wt%; Other is iron and inevitable trace impurity; Be organized as ferrite and martensite, ferrite volume parts is 89%, and martensite is 11%, yield strength R
p0.2for 405MPa, tensile strength Rm is 638MPa, and yield tensile ratio is 0.63, A
80be that 27%, n value is 0.16.
Embodiment 4
Slab chemical composition is designated as carbon: 0.07wt% by weight percentage; Chromium: 0.55wt%; Silicon: 0.04wt%; Manganese: 0.90wt%; Phosphorus: 0.015wt%; Sulphur: 0.0008wt%; Aluminium: 0.04wt%; [O]: 0.0030wt%; [N]: 0.0032wt%; Other is iron and inevitable trace impurity.
Production technique is as follows:
(1) by thickness, be 230mm heating of plate blank, control 1240 ℃ of Heating temperatures, soaking time is 35 minutes, 1250 ℃ of tapping temperatures.
(2) steel plate target rolling thickness specifications vary is 3mm, adopts the rolling of 7.5m/s constant speedpump.
(3) slab is rolled, it is 990 ℃ that roughing final temperature is controlled; It is 850 ℃ that finish rolling final temperature is controlled; Finish rolling total deformation 85%.
(4) after finish rolling, carry out cooling control, the target temperature of first paragraph cooling by water is 670～690 ℃, then carries out the air cooling of 6s, finally carries out water-cooled, and coiling temperature is controlled at 60 ℃.
The chemical composition of the dual phase steel of producing is carbon: 0.07wt%; Chromium: 0.55wt%; Silicon: 0.04wt%; Manganese: 0.90wt%; Phosphorus: 0.015wt%; Sulphur: 0.0008wt%; Aluminium: 0.04wt%; [O]: 0.0030wt%; [N]: 0.0032wt%; Other is iron and inevitable trace impurity; Be organized as ferrite and martensite, ferrite volume parts is 91%, and martensite is 9%, yield strength R
p0.2for 368MPa, tensile strength Rm is 610MPa, and yield tensile ratio is 0.60, A
80be that 25%, n value is 0.17.
Embodiment 5
Slab chemical composition is designated as carbon: 0.10wt% by weight percentage; Chromium: 0.58wt%; Silicon: 0.1wt%; Manganese: 0.9wt%; Phosphorus: 0.008wt%; Sulphur: 0.0015wt%; Aluminium: 0.05wt%; [O]: 0.0028wt%; [N]: 0.0029wt%; Other is iron and inevitable trace impurity.
Production technique is as follows:
(1) by thickness, be 230mm heating of plate blank, control 1240 ℃ of Heating temperatures, soaking time is 25 minutes, 1260 ℃ of tapping temperatures.
(2) steel plate target rolling thickness specifications vary is 3.5mm, adopts the rolling of 7m/s constant speedpump.
(3) slab is rolled, it is 1060 ℃ that roughing final temperature is controlled; It is 860 ℃ that finish rolling final temperature is controlled; Finish rolling total deformation 95%.
(4) after finish rolling, carry out cooling control, the target temperature of first paragraph cooling by water is 680～720 ℃, then carries out the air cooling of 8.5s, finally carries out water-cooled, and coiling temperature is controlled at 100 ℃.
The chemical composition of the dual phase steel of producing is carbon: 0.10wt%; Chromium: 0.58wt%; Silicon: 0.1wt%; Manganese: 0.9wt%; Phosphorus: 0.008wt%; Sulphur: 0.0015wt%; Aluminium: 0.05wt%; [O]: 0.0028wt%; [N]: 0.0029wt%; Other is iron and inevitable trace impurity; Be organized as ferrite and martensite, ferrite volume parts is 89%, and martensite is 11%, yield strength R
p0.2for 382MPa, tensile strength Rm is 626MPa, and yield tensile ratio is 0.61, A
80be that 22%, n value is 0.16.
Embodiment 6
Slab chemical composition is designated as carbon: 0.11wt% by weight percentage; Chromium: 0.42wt%; Silicon: 0.02wt%; Manganese: 1.06wt%; Phosphorus: 0.011wt%; Sulphur: 0.001wt%; Aluminium: 0.03wt%; [O]: 0.0016wt%; [N]: 0.0030wt%; Other is iron and inevitable trace impurity.
Production technique is as follows:
(1) by thickness, be 230mm heating of plate blank, control 1240 ℃ of Heating temperatures, soaking time is 35 minutes, 1270 ℃ of tapping temperatures.
(2) steel plate target rolling thickness specifications vary is 4.8mm, adopts the rolling of 5.2m/s constant speedpump.
(3) slab is rolled, it is 1070 ℃ that roughing final temperature is controlled; It is 850 ℃ that finish rolling final temperature is controlled; Finish rolling total deformation 82%.
(4) after finish rolling, carry out cooling control, the target temperature of first paragraph cooling by water is 710～730 ℃, then carries out the air cooling of 9s, finally carries out water-cooled, and coiling temperature is controlled at 50 ℃.
The chemical composition of the dual phase steel of producing is carbon: carbon: 0.11wt%; Chromium: 0.42wt%; Silicon: 0.02wt%; Manganese: 1.06wt%; Phosphorus: 0.011wt%; Sulphur: 0.001wt%; Aluminium: 0.03wt%; [O]: 0.0016wt%; [N]: 0.0030wt%; Other is iron and inevitable trace impurity; Be organized as ferrite and martensite, ferrite volume parts is 90%, and martensite is 10%, yield strength R
p0.2for 405MPa, tensile strength Rm is 623MPa, and yield tensile ratio is 0.65, A
80be that 21%, n value is 0.16.
It should be noted last that, above embodiment is only unrestricted in order to technical scheme of the present invention to be described, although the present invention is had been described in detail with reference to example, those of ordinary skill in the art is to be understood that, can modify or be equal to replacement technical scheme of the present invention, and not departing from the spirit and scope of technical solution of the present invention, it all should be encompassed in the middle of claim scope of the present invention.
Claims (6)
1. containing a Cr hot-rolled dual-phase steel, it is characterized in that, its chemical composition mass percent is:
C:0.06～0.12wt%; Cr:0.40～0.60%; Si:0.02～0.20%; Mn :≤1.20wt%; P :≤0.015wt%; S :≤0.008wt%; Al:0.02～0.06wt%; [O] :≤0.003wt%; [N] :≤0.005wt%; Other is iron and inevitable trace impurity.
2. produce a method for dual phase steel as claimed in claim 1, it is characterized in that, comprising:
After being heated by process furnace, slab carries out soaking;
Slab after described soaking is carried out to roughing, finish rolling acquisition hot-rolled sheet;
Described hot-rolled sheet is carried out after cooling batching acquisition finished product, and coiling temperature is controlled at below 200 ℃.
3. method as claimed in claim 2, is characterized in that:
Described while carrying out soaking after slab is heated by process furnace, Heating temperature is 1220～1280 ℃, and soaking time is 20～40 minutes, and tapping temperature is controlled at 1200～1280 ℃.
4. method as claimed in claim 2, is characterized in that:
It is 980～1080 ℃ that described roughing final temperature is controlled, and it is 780～900 ℃ that finish rolling final temperature is controlled, and finish rolling total deformation is greater than 80%.
5. method as claimed in claim 2, is characterized in that:
When roughing, finish rolling, adopt constant speed rolling, hot-rolled sheet thickness specification variation range is controlled at 2～5mm, and roll speed, because of variation in thickness, is controlled at 5～10m/s.
6. method as claimed in claim 2, is characterized in that:
Described hot-rolled sheet is carried out when cooling, first the hot-rolled sheet after finish rolling is carried out fast coolingly, cooling target temperature is 670～730 ℃, and then carries out the air cooling of 5～10s, finally carries out water-cooled again.
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| CN106086627A (en) * | 2016-07-27 | 2016-11-09 | 武汉钢铁股份有限公司 | A kind of 600MPa level hot-rolled dual-phase steel and production method thereof |
| CN107829025A (en) * | 2017-10-19 | 2018-03-23 | 武汉钢铁有限公司 | A kind of Thin Specs have the dual phase steel and its processing method of good reaming performance |
| CN110000207A (en) * | 2019-03-29 | 2019-07-12 | 山东钢铁集团日照有限公司 | A kind of manufacturing method of high surface grade hot rolling acid-cleaning dual phase steel |
| CN110614278A (en) * | 2019-10-25 | 2019-12-27 | 攀钢集团攀枝花钢铁研究院有限公司 | Rolling method of hot-rolled dual-phase steel |
| CN112458358A (en) * | 2020-10-26 | 2021-03-09 | 首钢集团有限公司 | 500 MPa-grade hot-rolled phase-change reinforced steel and preparation method and application thereof |
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| CN101857942A (en) * | 2010-07-06 | 2010-10-13 | 攀钢集团钢铁钒钛股份有限公司 | Hot rolled steel plate with 590MPa-level tensile strength and production method thereof |
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- 2013-10-14 CN CN201310479360.XA patent/CN103540849A/en active Pending
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| CN101857942A (en) * | 2010-07-06 | 2010-10-13 | 攀钢集团钢铁钒钛股份有限公司 | Hot rolled steel plate with 590MPa-level tensile strength and production method thereof |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106086627A (en) * | 2016-07-27 | 2016-11-09 | 武汉钢铁股份有限公司 | A kind of 600MPa level hot-rolled dual-phase steel and production method thereof |
| CN107829025A (en) * | 2017-10-19 | 2018-03-23 | 武汉钢铁有限公司 | A kind of Thin Specs have the dual phase steel and its processing method of good reaming performance |
| CN110000207A (en) * | 2019-03-29 | 2019-07-12 | 山东钢铁集团日照有限公司 | A kind of manufacturing method of high surface grade hot rolling acid-cleaning dual phase steel |
| CN110614278A (en) * | 2019-10-25 | 2019-12-27 | 攀钢集团攀枝花钢铁研究院有限公司 | Rolling method of hot-rolled dual-phase steel |
| CN112458358A (en) * | 2020-10-26 | 2021-03-09 | 首钢集团有限公司 | 500 MPa-grade hot-rolled phase-change reinforced steel and preparation method and application thereof |
| CN112458358B (en) * | 2020-10-26 | 2022-03-22 | 首钢集团有限公司 | 500 MPa-grade hot-rolled phase-change reinforced steel and preparation method and application thereof |
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Application publication date: 20140129 |