CN110066966A - A kind of low internal stress titaniferous high-strength steel and production method - Google Patents
A kind of low internal stress titaniferous high-strength steel and production method Download PDFInfo
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- CN110066966A CN110066966A CN201910430932.2A CN201910430932A CN110066966A CN 110066966 A CN110066966 A CN 110066966A CN 201910430932 A CN201910430932 A CN 201910430932A CN 110066966 A CN110066966 A CN 110066966A
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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Abstract
The present invention relates to a kind of low internal stress titaniferous high-strength steel, steel plate chemical component mass percents are as follows: C:0.06%~0.11%, Si:0.10%~0.25%, Mn:1.1%~1.4%, P≤0.015%, S≤0.005%, Ti:0.06%~0.10%, Nb:0.010%~0.030%, N≤0.005%, Als:0.02%~0.05%, Mn/C:13%~17%, Ti/Nb:3.5%~4.5%, remaining is Fe and impurity.Using blast-melted, desulfurizing iron, converter smelting, LF+RH refining, continuous casting, hot-loading and hot-conveying, heating, rolling, section cooling, batches, opens flat finishing, heat treatment process route.Internal stress absolute value is low, and uniformity is high；Transverse and longitudinal buckling performance is excellent, and up to d=a, 180 ° of qualifications, warpage, straightness be not excellent for the bending of overall length direction.
Description
Technical field
The present invention relates to high-strength steel manufacturing field more particularly to a kind of low internal stress titaniferous high-strength steel and production methods.
Background technique
Low-alloy high-strength steel is the high-strength steel that the microalloy elements such as Mo, Nb, V, Ti are added on the basis of C-Mn steel, in engineering
The industries such as machinery are used widely, as intensity rank is constantly promoted, the cooling uniformity and stability control of the operation of rolling
Difficulty is increasing, directly affects internal stress and production board shape, even if after being aligned by high-strength straightening equipment, can obtain preferably
Strip shape quality, but after user's flame or plasma cut, steel plate in the case where non-uniform temperature influences, release by internal stress
It puts, causes the secondary warpage of steel plate and deformation, it is difficult to continue to use.To reduce internal stress, part steel mill using hot rolled coil slow cooling or
Bell-type annealing furnace annealing has certain effect, but internal stress elimination is not enough and uniformly, still influences subsequent use.
The patent of invention of publication number CN104264052A discloses a kind of steel for engineering machinery plate and its production method, steel plate
Chemical component mass percentage are as follows: C0.05~0.09, Si0.05~0.30, Mn1.5~2.0, P≤0.025, S≤
0.005, Nb0~0.07, Ti0.08~0.15, Mo0.10~0.30, Als0.015~0.06, Ca0.0010~0.0030, N≤
0.006, surplus Fe, steel plate thickness are 3.0mm~8.5mm.Its intensity and elongation percentage are more than needed big, and impact flexibility is good, postwelding
Lose that strong rate is small, but finishing temperature and the gap of coiling temperature are larger, cooling stability control acquires a certain degree of difficulty, and will affect reel volume
Shape and plate shape, other Mo containing precious metal, and using individual tempering, affect cost of alloy and production efficiency.
The patent of invention of publication number CN102864295A discloses a kind of elimination tensile strength >=thin steel of 785MPa level structure
The method of plate stress, step: setting normalizing furnace eliminates the technological parameter of stress: the frequency conversion matching speed of roller-way 2.0 ±
0.03 meter per second, the linear velocity of roller-way is in 0.01~0.33 meter per second, signal accuracy≤300mm of steel plate running position；It eliminates
Stress: being transported to the furnace entry table in normalizing furnace for whole steel plated and eliminate stress, eliminates the temperature of stress at 500~580 DEG C, disappears
The time of de-stress is that additional at least 30 whole steel plated height are controlled at 15~40 millimeters the high degree of whole steel plated (millimeter) again；Out
Furnace is simultaneously air-cooled to room temperature.The present invention can make answering for steel plate under the premise of guaranteeing 8 millimeters or less thin specification steel plate mechanical properties
Power control is being no more than 32MPa, keeps steel plate indeformable, meets the requirement of user, but the patent is only limitted to by heat
Reason means reduce internal stress, and control measures are single, and the state of different material is not distinguished, if raw material internal stress is excessive,
It is subject to certain restrictions using the effect of this method.
The patent of invention of publication number CN106319389A disclose low cost, high machining property steel for engineering machinery and
Its manufacturing method, composition by weight percent are as follows: C 0.06~0.10%, Si 0.30~0.60%, Mn 1.00~1.60%,
P≤0.015%, S≤0.0030%, Ni 0.20~0.60%, Cr 0.50~0.80%, Mo 0.25~0.55%, V
0.025~0.065%, B 0.0008~0.0020%, Ti 0.008~0.018%, Al 0.030~0.070%, N≤
0.0050%, Ca 0.0010~0.0040%, remaining Fe and unavoidably it is mingled with；Mn/C >=15,415≤steel plate quenching temperature ×
[(%Cr)+3.3 (%Mo)+1.75 (%V)+2.15 (%Si)] }/[11.7 (%C) 1/2+1.23 (%Mn)+0.36 (%Cu)+
(%Ni)]≤565, Ca/S be 0.80~1.50,2.5 × 10-6≤(%Ca) × (%S)≤2.5 × 10-3.Using controlled rolling+
Two-phase section hardening and tempering process combines, while obtaining high-intensitive, low-temperature flexibility, the cold machining mouldability, weldability of steel plate
And antifatigue shock load characteristic is similarly excellent.But it is containing higher Cr, Ni, Mo etc., and cost of alloy is high, and process flow
It is long, there is higher difficulty in terms of marketing application.In addition, not referring to steel plate internal stress situation.
Summary of the invention
Technical problem to be solved by the invention is to provide a kind of low internal stress titaniferous high-strength steel and production methods, to overcome
Above-mentioned deficiency in the prior art.
The technical scheme to solve the above technical problems is that a kind of low internal stress titaniferous high-strength steel, steel plate chemistry
Ingredient percent are as follows: C:0.06%~0.11%, Si:0.10%~0.25%, Mn:1.1%~1.4%, P≤
0.015%, S≤0.005%, Ti:0.06%~0.10%, Nb:0.010%~0.030%, N≤0.005%, Als:
0.02%~0.05%, Mn/C:13%~17%, Ti/Nb:3.5%~4.5%, remaining is Fe and impurity.
A kind of low internal stress titaniferous high-strength steel production method:
Using blast-melted, desulfurizing iron, converter smelting, LF+RH refining, continuous casting, hot-loading and hot-conveying, heating, rolling, laminar flow
It cools down, batch, opening flat finishing, heat treatment process route；
Technological parameter is as follows:
Hot-loading and hot-conveying: being transported to slow cooling before heating furnace after continuous casting steel billet is offline, hot charging charging temperature is greater than 400 DEG C；
Heating: 1200 DEG C~1250 DEG C of tapping temperature, heating time >=140min；
Rolling: it is rolled using two-stage control, 1020 DEG C~1060 DEG C of roughing outlet temperature, 790 DEG C of finish rolling finishing temperature
~830 DEG C；
Section cooling: using turning cold but speed control, beginning to cool 20 DEG C/s~30 DEG C of speed/s, with cooling procedure into
Capable and steel roll temperature reduces, and cooling rate is linearly decreased to 10 DEG C/s substantially hereinafter, coiling temperature is 490 DEG C~530 DEG C；
It opens flat finishing: carrying out out flat, and be packaged；
Heat treatment: using whole packet tempering heat treatment, and tempering temperature is 520 DEG C~620 DEG C, and soaking time is (the thick value+60 of packet
~80) min.
In the above scheme, Bao Houwei 15mm~50mm in flat finishing is opened.
The beneficial effects of the present invention are:
1) internal stress absolute value is low, and uniformity is high；
2) transverse and longitudinal buckling performance is excellent, and up to d=a, (d=Bend diameter, a=steel plate nominal are thick for 180 ° of qualifications
Degree), warpage, straightness be not excellent for the bending of overall length direction；
3) alloy content is low, low in cost, is suitable for construction machinery industry crane, the contour peace of aerial work platform boom
Full property requires the use of component.
Detailed description of the invention
Fig. 1 is internal stress detection schematic diagram；
Fig. 2 is internal stress tendency chart；
Fig. 3 is the flow chart of low internal stress titaniferous high-strength steel production method.
Specific embodiment
The principle and features of the present invention will be described below with reference to the accompanying drawings, and the given examples are served only to explain the present invention, and
It is non-to be used to limit the scope of the invention.
A kind of low internal stress titaniferous high-strength steel, steel plate chemical component mass percent are as follows: C:0.06%~0.11%, Si:
0.10%~0.25%, Mn:1.1%~1.4%, P≤0.015%, S≤0.005%, Ti:0.06%~0.10%, Nb:
0.010%~0.030%, N≤0.005%, Als:0.02%~0.05%, Mn/C:13%~17%, Ti/Nb:3.5%~
4.5%, remaining is Fe and impurity.
As shown in figure 3, a kind of low internal stress titaniferous high-strength steel production method, comprises the technical steps that:
Using blast-melted, desulfurizing iron, converter smelting, LF+RH refining, continuous casting, hot-loading and hot-conveying, heating, rolling, laminar flow
It cools down, batch, opening flat finishing, heat treatment process route；
Technological parameter is as follows:
Thickness range 3mm~16mm；
Hot-loading and hot-conveying: under continuous casting steel billet after wire cutting, being transported to slow cooling before heating furnace, and hot charging charging temperature is greater than 400 DEG C, can
Steel billet cooling-heating course is reduced, tissue and crystal grain is promoted to homogenize；
Heating: 1200 DEG C~1250 DEG C of tapping temperature, heating time >=140min guarantees Nb, V, Ti alloying element and carbon
Nitride is dissolved completely, prevents bulky grain precipitated phase from becoming field trash, influences internal stress distribution；
Rolling: it is rolled using two-stage control, 1020 DEG C~1060 DEG C of roughing outlet temperature, 790 DEG C of finish rolling finishing temperature
, when recrystallization zone rolls, rolling pass is reduced under equipment enabled condition, improves percentage pass reduction, to increase deformation by~830 DEG C
The recrystallization quantity of austenite when non-recrystallization zone rolls, guarantees that total reduction is greater than 65%, it is difficult to understand in non-recrystallization to increase material
The deformation in the area Shi Ti increases the dislocation in deformed austenite, it is uniform to be conducive to fine microstructures；
It is to prevent from controlling cold process to reduce the intensity of cooling in section cooling stage using lower finishing temperature range
Middle because intensity of cooling is excessive, steel plate generates biggish internal stress, comprehensively considers, 790 DEG C~830 DEG C of finish rolling finishing temperature are advisable；
Section cooling: using turning cold but speed control, beginning to cool 20 DEG C/s~30 DEG C of speed/s, with cooling procedure into
Capable and steel roll temperature reduces, and cooling rate is linearly decreased to 10 DEG C/s substantially hereinafter, coiling temperature is 490 DEG C~530 DEG C；
It is that need to be cooled to bainite range as early as possible because beginning to cool the stage, obtain shellfish why using variation cooling velocity
Family name's body tissue, proof strength, cooling rate are gradually reduced, and are because steel plate returns red process, and steel plate is thicker, returns in cooling procedure
Red effect is stronger, reduces intensity of cooling and speed is conducive to thickness direction even tissue, reduce thickness direction stress.Cooling velocity
It gradually decreases, is conducive to obtain stable coiling temperature, it is even more so for thicker steel plate, it may advantageously facilitate length side
Inside stress uniformity significantly improves；
It opens flat finishing: flat equipment being opened using strength and carries out out flat, and is packaged as requested, Bao Houwei 15mm~
50mm；
Bao Houtai is thin, and destressing effect is relatively poor, because surface layer and center portion steel plate cooling rate are inconsistent in process air cooler,
And it is uneconomical.Bao Houtai is thick, and center portion steel billet temperature is difficult to reach target temperature, influences stress removal effect.The experiment proved that
Under different temperature (0 DEG C~30 DEG C), packet thickness 15mm~50mm is best, temperature and Bao Houcheng inverse correlation relationship；
Heat treatment: using whole packet tempering heat treatment, and tempering temperature is 520 DEG C~620 DEG C, and soaking time is (the thick value+60 of packet
~80) min；
Why whole packet tempering heat treatment is used, is the air-cooled cooling rate phase because compared with individual tempering, after whole packet tempering
To more slowly, whole steel plated structure property uniformity is higher, can achieve better destressing effect.
In the present invention composition range and technology point setting the reason is as follows that:
1) C is to improve the most cheap element of the strength of materials, and as phosphorus content increases, hardness, intensity are improved, but plasticity and toughness and
Welding performance reduces.Comprehensively consider, C weight percentage is 0.06%~0.11%；
2) in common solid solution element, Si is only second to P, is solid-solution in ferrite and austenite, and intensity can be improved, and Si can
Diffusion velocity of the carbon in ferrite is reduced, the carbide being precipitated when tempering is made to be not easy to assemble, improves temper resistance, but Si mistake
Height influences surface quality, comprehensively considers, and Si weight percentage is advisable for 0.10%~0.25%；
3) Mn significantly reduces the decomposition rate of the Ar1 temperature of steel, austenite, and intensity can be improved by being infinitely dissolved with Fe, but Mn
Content Ruo Taigao will increase steel belt roof bolt brittleness, leads to serious center segregation, comprehensively considers, and Mn weight percentage is
1.1%~1.4% is advisable.Meanwhile to reduce microstructure segregation degree and guaranteeing preferable harden ability, thickness direction group is significantly improved
Knit performance uniformity, reduce thickness direction internal stress absolute value, improve internal stress uniformity, Mn/C control 13%~17% it
Between be advisable；If Mn/C is too low, thickness direction especially core structure and textura epidermoidea's difference can be caused, Ruo Taigao not only makes
It is wasted at alloy, also center portion can be made Mn segregation occur, influence structure property and internal stress uniformity；
4) Nb: there is extremely strong affinity with C, N in steel, stable Nb (C, N) compound can be formed therewith, controlled
It induces and is precipitated in the operation of rolling, along austenite grain boundary Dispersed precipitate, as the nucleation mass point of phase transformation, can effectively prevent to recrystallize,
Ferrite nucleation rate is improved, it is significant to Grain refinement, comprehensively consider, Nb weight percentage is 0.010%~0.030%
It is advisable；
5) Ti and C, N element form TiN and TiC particle resistant to high temperature, play the role of precipitation strength, are pinned at prior austenite
Body crystal boundary prevents Austenite Grain Growth, and TiN and TiC particle significantly prevent heat affected area crystal grain from growing up when welding, improves and welds
Performance, when Ti content is lower, precipitation strength and welding performance improvement result are small, and when Ti too high levels, plasticity is reduced, and is held
Performance inconsistency is easily caused, is comprehensively considered, Ti weight percentage is advisable for 0.06%~0.10%；
6) influence of the N to steel performance is similar to C and P, and as N content increases, intensity is significantly improved, and plasticity is especially tough
Property significantly reduce, deteriorated weldability, cold brittleness aggravation, while increasing timeliness tendency, N and Ti have good affinity, are formed thick
Big TiN compound, when heating, are difficult to sufficiently dissolve, and form field trash, become the formation of crack in stretching and impact process, can also make
It wastes, therefore comprehensively considers at alloy, N≤0.005% is advisable；
7) Ti/Nb: taking Nb, Ti combined microalloying while also needing to guarantee that (Nb, Ti) (C, N) uniform particle is distributed in steel
In, play compound precipitation strength, meanwhile, comprehensively consider, Ti/Nb is advisable 3.5%~4.5%, in higher cooling velocity
Under, be conducive to save Nb alloying element, the refined crystalline strengthening effect of water consumption substitution part Nb achievees the purpose that with water for alloy, together
When also can guarantee intensity, but ratio Ruo Taigao then will affect the alloying element homogenization of continuous casting process, lead to steel plate interior tissue
There is not molten (the Nb, Ti) complex inclusion of bulky grain, structure property uniformity is not only influenced, also for the uniformity ten of internal stress
Divide nocuousness；
8) Als in steel can deoxidation, can also play the role of refine crystal grain, comprehensively consider, Als is 0.02%~0.05%
It is advisable；
9) P, S are harmful impurity elements in steel, and P forms segregation easily in steel in steel, reduce the toughness and weldability of steel
Can, S easily forms plasticity sulfide, and steel plate is made to generate layering, deteriorate plate property, therefore the lower P, S content the better, comprehensively considers,
It is P≤0.015%, S≤0.005% by P, S content of steel.
Examples 1 to 3, a kind of low internal stress titaniferous high-strength steel specifically each chemical component and its weight percent such as 1 institute of table
Show；Comparative example 1~2, chemical component and its weight percent are also as shown in table 1:
Table 1
The concrete technology data of production technology feature are shown in Table 2 in embodiment 1-3 and comparative example 1-2:
Table 2
According to GB/T228 and GB/T231 national standard, the low internal stress high-strength steel of testing example 1~3 and comparison
The performance of example 1-2 is as shown in table 3.
Table 3
As it can be seen that embodiment and comparative example tensile property is substantially at same level, but embodiment low-temperature impact work is relatively more
Height, this has certain relationship with lower internal stress and uniformity, from figure 2 it can be seen that the internal stress absolute value of embodiment is more
Small, uniformity is higher, and the internal stress uniformity of comparative example is poor.Fig. 1 is internal stress detection schematic diagram.
Although the embodiments of the present invention has been shown and described above, it is to be understood that above-described embodiment is example
Property, it is not considered as limiting the invention, those skilled in the art within the scope of the invention can be to above-mentioned
Embodiment is changed, modifies, replacement and variant.
Claims (3)
1. a kind of low internal stress titaniferous high-strength steel, it is characterised in that: steel plate chemical component mass percent are as follows: C:0.06%~
0.11%, Si:0.10%~0.25%, Mn:1.1%~1.4%, P≤0.015%, S≤0.005%, Ti:0.06%~
0.10%, Nb:0.010%~0.030%, N≤0.005%, Als:0.02%~0.05%, Mn/C:13%~17%, Ti/
Nb:3.5%~4.5%, remaining is Fe and impurity.
2. a kind of low internal stress titaniferous high-strength steel production method, it is characterised in that:
It is cold using blast-melted, desulfurizing iron, converter smelting, LF+RH refining, continuous casting, hot-loading and hot-conveying, heating, rolling, laminar flow
But, batch, open flat finishing, heat treatment process route；
Technological parameter is as follows:
Hot-loading and hot-conveying: being transported to slow cooling before heating furnace after continuous casting steel billet is offline, hot charging charging temperature is greater than 400 DEG C；
Heating: 1200 DEG C~1250 DEG C of tapping temperature, heating time >=140min；
Rolling: it is rolled using two-stage control, 1020 DEG C~1060 DEG C of roughing outlet temperature, finish rolling finishing temperature 790 DEG C~830
℃；
Section cooling: using turning cold but speed control, beginning to cool 20 DEG C/s~30 DEG C of speed/s, carry out with cooling procedure and
Steel roll temperature reduces, and cooling rate is linearly decreased to 10 DEG C/s substantially hereinafter, coiling temperature is 490 DEG C~530 DEG C；
It opens flat finishing: carrying out out flat, and be packaged；
Heat treatment: using whole packet tempering heat treatment, and tempering temperature is 520 DEG C~620 DEG C, soaking time be (the thick value of packet+60~
80)min。
3. a kind of low internal stress titaniferous high-strength steel production method according to claim 2, which is characterized in that described to open flat essence
Whole middle Bao Houwei 15mm~50mm.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN111235480A (en) * | 2020-03-17 | 2020-06-05 | 本钢板材股份有限公司 | Preparation method of high-strength steel coil |
| CN111304538A (en) * | 2020-03-31 | 2020-06-19 | 武汉钢铁有限公司 | Low-cost hot-rolled ultrahigh-strength steel and manufacturing method thereof |
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