CN110066966B - Low-internal-stress titanium-containing high-strength steel and production method thereof - Google Patents
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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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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
Abstract
The invention relates to a low internal stress titanium-containing high-strength steel, which comprises the following chemical components in percentage by mass: c: 0.06% -0.11%, Si: 0.10-0.25%, Mn: 1.1-1.4%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Ti: 0.06% -0.10%, Nb: 0.010-0.030 percent, N is less than or equal to 0.005 percent, Als: 0.02% -0.05%, Mn/C: 13% -17%, Ti/Nb: 3.5 to 4.5 percent, and the balance of Fe and impurities. The method adopts the process routes of blast furnace molten iron, molten iron desulphurization, converter smelting, LF + RH refining, continuous casting, hot charging and hot conveying, heating, rolling, laminar cooling, coiling, flattening and finishing and heat treatment. The absolute value of the internal stress is low, and the uniformity is high; the transverse and longitudinal bending performance is excellent, d is a, 180 degrees are qualified, the bending in the full length direction is not warped, and the straightness is excellent.
Description
Technical Field
The invention relates to the field of high-strength steel manufacturing, in particular to low-internal-stress titanium-containing high-strength steel and a production method thereof.
Background
The low-alloy high-strength steel is high-strength steel added with micro-alloy elements such as Mo, Nb, V, Ti and the like on the basis of C-Mn steel, is widely applied to industries such as engineering machinery and the like, and has the advantages that the cooling uniformity and the stability control difficulty in the rolling process are increased along with the continuous improvement of the strength level, the internal stress and the finished product plate shape are directly influenced, even if the steel plate is straightened by high-strength straightening equipment, better plate shape quality can be obtained, once the steel plate is cut by flame or plasma of a user, the internal stress is released under the condition of uneven temperature influence, the secondary warping and deformation of the steel plate are caused, and the steel plate is difficult to continue to use. In order to reduce the internal stress, a part of steel mills adopt slow cooling of hot rolled coils or annealing of a hood-type annealing furnace, which has certain effect, but the internal stress is not sufficiently and uniformly eliminated, and the subsequent use is still influenced.
The invention patent of publication No. CN104264052A discloses a steel plate for engineering machinery and a production method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: 0.05-0.09% of C, 0.05-0.30% of Si, 1.5-2.0% of Mn, less than or equal to 0.025% of P, less than or equal to 0.005% of S, 0-0.07% of Nb, 0.08-0.15% of Ti, 0.10-0.30% of Mos, 0.015-0.06% of Als, 0.0010-0.0030% of Ca0, less than or equal to 0.006% of N, and the balance of Fe, wherein the thickness of the steel plate is 3.0-8.5 mm. The alloy has the advantages of large surplus of strength and elongation, good impact toughness, small post-welding strength loss rate, large difference between the final rolling temperature and the coiling temperature, difficult control of cooling stability, influence on the coil shape and the plate shape of an original coil, precious metal Mo contained in the alloy, and influence on the alloy cost and the production efficiency by single tempering.
The invention patent of publication No. CN102864295A discloses a method for eliminating the stress of a steel sheet with a tensile strength of more than or equal to 785MPa grade structure, which comprises the following steps: setting technological parameters of the normalizing furnace for stress relief: the frequency conversion matching speed of the roller way is 2.0 +/-0.03 m/s, the linear speed of the roller way is 0.01-0.33 m/s, and the signal accuracy of the running position of the steel plate is less than or equal to 300 mm; stress relief: conveying the whole steel plate package to a furnace inlet roller way in a normalizing furnace and eliminating stress, wherein the temperature for eliminating the stress is 500-580 ℃, the time for eliminating the stress is the height (mm) of the whole steel plate package, and the height of at least 30 whole steel plate packages is controlled to be 15-40 mm; discharging and air cooling to room temperature. On the premise of ensuring the mechanical property of a thin steel plate with the thickness of below 8 mm, the invention can control the stress of the steel plate to be not more than 32MPa, so that the steel plate is not deformed, and the use requirements of users are met.
The invention patent of publication No. CN106319389A discloses a low-cost and high-machinability steel for engineering machinery and a manufacturing method thereof, wherein the steel comprises the following components in percentage by weight: 0.06-0.10% of C, 0.30-0.60% of Si, 1.00-1.60% of Mn, less than or equal to 0.015% of P, less than or equal to 0.0030% of S, 0.20-0.60% of Ni, 0.50-0.80% of Cr, 0.25-0.55% of Mo, 0.025-0.065% of V, 0.0008-0.0020% of B, 0.008-0.018% of Ti, 0.030-0.070% of Al, less than or equal to 0.0050% of N, 0.0010-0.0040% of Ca, and the balance of Fe and inevitable impurities; Mn/C is more than or equal to 15, and 415 is less than or equal to { steel plate quenching temperature x [ (% 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 is 0.80-1.50, and 2.5 x 10 < -6 > < (% Ca) × (% S) < 2.5 x 10 < -3. The combination of controlled rolling and two-phase region quenching and tempering technology is adopted, so that high strength is obtained, and simultaneously, the low-temperature toughness, cold machining formability, weldability and fatigue impact load resistance of the steel plate are also excellent. But the alloy contains higher Cr, Ni, Mo and the like, has high alloy cost, long process flow and higher difficulty in the aspect of market popularization and application. In addition, no mention is made of the internal stress of the steel sheet.
Disclosure of Invention
The invention aims to solve the technical problem of providing low-internal-stress titanium-containing high-strength steel and a production method thereof so as to overcome the defects in the prior art.
The technical scheme for solving the technical problems is as follows: the low-internal-stress titanium-containing high-strength steel comprises the following chemical components in percentage by mass: c: 0.06% -0.11%, Si: 0.10-0.25%, Mn: 1.1-1.4%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Ti: 0.06% -0.10%, Nb: 0.010-0.030 percent, N is less than or equal to 0.005 percent, Als: 0.02% -0.05%, Mn/C: 13% -17%, Ti/Nb: 3.5 to 4.5 percent, and the balance of Fe and impurities.
A production method of low-internal-stress titanium-containing high-strength steel comprises the following steps:
adopting a blast furnace molten iron, molten iron desulphurization, converter smelting, LF + RH refining, continuous casting, hot charging and hot conveying, heating, rolling, laminar cooling, coiling, flattening and finishing, and heat treatment process route;
the technological parameters are as follows:
hot charging and hot conveying: after the continuous casting plate blank is off-line, the continuous casting plate blank is conveyed to the front of a heating furnace for slow cooling, and the hot charging temperature is more than 400 ℃;
heating: the tapping temperature is 1200-1250 ℃, and the heating time is more than or equal to 140 min;
rolling: two-stage controlled rolling is adopted, wherein the outlet temperature of rough rolling is 1020-1060 ℃, and the finish rolling temperature of finish rolling is 790-830 ℃;
laminar cooling: the variable cooling speed control is adopted, the cooling speed is started to be 20 ℃/s-30 ℃/s, the cooling speed is basically linearly reduced to be below 10 ℃/s along with the cooling process and the temperature of the steel coil is reduced, and the coiling temperature is 490-530 ℃;
leveling and finishing: opening and flattening, and packaging;
and (3) heat treatment: and (3) carrying out tempering heat treatment on the whole package, wherein the tempering temperature is 520-620 ℃, and the heat preservation time is (package thickness value + 60-80) min.
In the scheme, the thickness of the secondary package in the open flat finishing is 15 mm-50 mm.
The invention has the beneficial effects that:
1) the absolute value of the internal stress is low, and the uniformity is high;
2) the transverse and longitudinal bending performance is excellent, d is a, 180 degrees are qualified (d is the bending core diameter, and a is the nominal thickness of the steel plate), the bending in the full length direction is not warped, and the flatness is excellent;
3) the alloy has low content and low cost, and is suitable for high-safety-requirement parts such as cranes, suspension arms of aerial work platforms and the like in the engineering machinery industry.
Drawings
FIG. 1 is a schematic diagram of an internal stress test;
FIG. 2 is a graph of internal stress trend;
FIG. 3 is a flow chart of a production method of low internal stress titanium-containing high-strength steel.
Detailed Description
The principles and features of this invention are described below in conjunction with the following drawings, which are set forth by way of illustration only and are not intended to limit the scope of the invention.
The low-internal-stress titanium-containing high-strength steel comprises the following chemical components in percentage by mass: c: 0.06% -0.11%, Si: 0.10-0.25%, Mn: 1.1-1.4%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Ti: 0.06% -0.10%, Nb: 0.010-0.030 percent, N is less than or equal to 0.005 percent, Als: 0.02% -0.05%, Mn/C: 13% -17%, Ti/Nb: 3.5 to 4.5 percent, and the balance of Fe and impurities.
As shown in FIG. 3, the production method of the low internal stress titanium-containing high-strength steel comprises the following process steps:
adopting a blast furnace molten iron, molten iron desulphurization, converter smelting, LF + RH refining, continuous casting, hot charging and hot conveying, heating, rolling, laminar cooling, coiling, flattening and finishing, and heat treatment process route;
the technological parameters are as follows:
the thickness range is 3 mm-16 mm;
hot charging and hot conveying: after the continuous casting plate blank is cut off from the line, the continuous casting plate blank is conveyed to a heating furnace for slow cooling, the temperature of hot charging in the furnace is more than 400 ℃, the cooling-heating process of the steel blank can be reduced, and the homogenization of the structure and the crystal grains is promoted;
heating: the tapping temperature is 1200-1250 ℃, the heating time is more than or equal to 140min, the complete solid solution of Nb, V and Ti alloy elements and carbonitride is ensured, and large-particle precipitated phases are prevented from becoming inclusions to influence the internal stress distribution;
rolling: the two-stage controlled rolling is adopted, the rough rolling outlet temperature is 1020-1060 ℃, the finish rolling temperature is 790-830 ℃, when the recrystallization zone is used for rolling, the rolling passes are reduced under the condition of equipment permission, the pass reduction rate is improved, the recrystallization quantity of the deformed austenite is increased, when the non-recrystallization zone is used for rolling, the total reduction rate is ensured to be more than 65%, the deformation of the material in the non-recrystallization austenite zone is increased, the dislocation in the deformed austenite is increased, and the fine and uniform structure is facilitated;
the lower finishing temperature range is adopted for reducing the cooling strength in the laminar cooling stage and preventing the steel plate from generating larger internal stress due to overlarge cooling strength in the cooling control process, and the finishing temperature of finish rolling is preferably 790-830 ℃ in comprehensive consideration;
laminar cooling: the variable cooling speed control is adopted, the cooling speed is started to be 20 ℃/s-30 ℃/s, the cooling speed is basically linearly reduced to be below 10 ℃/s along with the cooling process and the temperature of the steel coil is reduced, and the coiling temperature is 490-530 ℃;
the reason that the cooling speed is changed is that the steel plate needs to be cooled to a bainite area as soon as possible in the cooling stage to obtain a bainite structure, the strength is guaranteed, and the cooling speed is gradually reduced. The cooling speed is gradually reduced, which is favorable for obtaining stable coiling temperature, especially for thicker steel plates, and is favorable for promoting the uniformity of internal stress in the length direction to be obviously improved;
leveling and finishing: opening and flattening by adopting a powerful opening and flattening device, and packaging according to requirements, wherein the package thickness is 15-50 mm;
the thickness of the clad is too thin, the stress relief effect is relatively poor, and the cooling speed of the surface layer steel plate and the core steel plate is not consistent in the air cooling process and is not economical. The cladding thickness is too thick, the core steel plate temperature is difficult to reach the target temperature, and the stress removal effect is influenced. Experiments prove that the bag thickness is optimal between 15mm and 50mm under different air temperatures (between 0 and 30 ℃), and the air temperature and the bag thickness are in an inverse correlation relationship;
and (3) heat treatment: tempering heat treatment is carried out on the whole package, the tempering temperature is 520-620 ℃, and the heat preservation time is (the package thickness value is plus 60-80) min;
the whole package tempering heat treatment is adopted because compared with single piece tempering, the air cooling speed after the whole package tempering is slower, the structure performance uniformity of the whole package steel plate is higher, and a better stress relief effect can be achieved.
The reasons for setting the component range and the process key point in the invention are as follows:
1) c is the cheapest element for improving the strength of the material, and the hardness and the strength are improved with the increase of the carbon content, but the ductility and the toughness and the welding performance are reduced. Comprehensively considering, the weight percentage of C is 0.06% -0.11%;
2) in common solid solution elements, Si is only second to P and is dissolved in ferrite and austenite in a solid manner, so that the strength can be improved, the Si can reduce the diffusion speed of carbon in the ferrite, carbides precipitated during tempering are not easy to aggregate, the tempering stability is improved, but the surface quality is influenced by overhigh Si, and the Si is preferably 0.10-0.25 percent by weight in comprehensive consideration;
3) mn obviously reduces the Ar1 temperature of the steel, the decomposition speed of austenite and the infinite solid solution energy of Fe to improve the strength, but if the Mn content is too high, the temper brittleness of the steel is increased, so that serious center segregation is caused, and the Mn content is 1.1-1.4 percent in percentage by weight in comprehensive consideration. Meanwhile, in order to reduce the structure segregation degree and ensure better hardenability, obviously improve the structure performance uniformity in the thickness direction, reduce the absolute value of the internal stress in the thickness direction and improve the internal stress uniformity, the Mn/C is preferably controlled between 13 percent and 17 percent; if the Mn/C is too low, the difference between the thickness direction, particularly the core structure and the surface structure can be caused, and if the Mn/C is too high, not only alloy waste is caused, but also Mn segregation can occur in the core, and the structure performance and the internal stress uniformity are influenced;
4) nb: the high-strength Nb-containing austenite grain boundary phase-change material has strong affinity with C, N in steel, can form a stable Nb (C, N) compound with the steel, is induced to separate out in the controlled rolling process, is dispersed and distributed along the austenite grain boundary, is used as a phase-change nucleation mass point, can effectively prevent recrystallization, improves the ferrite nucleation rate, has obvious effect on grain refinement, and is suitable for the Nb content of 0.010-0.030 percent by weight in comprehensive consideration;
5) ti and C, N elements form high-temperature resistant TiN and TiC particles to play a role in precipitation strengthening, the TiN and TiC particles are pinned at the original austenite crystal boundary to prevent austenite crystal grains from growing large, the TiN and TiC particles obviously prevent heat affected zone crystal grains from growing large during welding and improve welding performance, when the Ti content is low, the effects of precipitation strengthening and improving welding performance are small, when the Ti content is too high, the plasticity is reduced, and performance fluctuation is easy to cause, and the Ti weight percentage content is preferably 0.06-0.10 percent in comprehensive consideration;
6) the influence of N on the steel performance is similar to that of C and P, the strength is obviously improved along with the increase of N content, the plasticity, particularly the toughness is obviously reduced, the weldability is worsened, the cold brittleness is intensified, the aging tendency is increased, N and Ti have good affinity to form a thick TiN compound, the thick TiN compound is difficult to fully dissolve during heating to form inclusions which become crack sources in the stretching and impacting processes and can also cause alloy waste, so that the comprehensive consideration that N is less than or equal to 0.005 percent is favorable;
7) Ti/Nb: the composite microalloying of Nb and Ti is adopted, and meanwhile, the uniform distribution of (Nb, Ti) (C, N) particles in steel is ensured to play a role in composite precipitation strengthening, meanwhile, the Ti/Nb content is preferably 3.5-4.5%, the Nb alloy elements are saved at a higher cooling speed, water is used for replacing the fine-grain strengthening effect of partial Nb, the aim of replacing the alloy with water is achieved, the strength can be ensured, if the ratio is too high, the homogenization of the alloy elements in the continuous casting process can be influenced, large-particle undissolved (Nb, Ti) composite inclusions can be caused to appear in the internal structure of the steel plate, the uniformity of the structural performance is influenced, and the uniformity of the internal stress is very harmful;
8) als can be deoxidized in steel and can also play a role in refining grains, and the Als is preferably 0.02-0.05 percent in comprehensive consideration;
9) p, S is a harmful impurity element in steel, P in steel is easy to form segregation in steel, the toughness and welding performance of steel are reduced, S is easy to form plastic sulfide, steel plate is layered, and the performance of steel plate is deteriorated, so the lower the P, S content is, the better, the comprehensive consideration is that the P, S content of steel is P less than or equal to 0.015 percent, and S less than or equal to 0.005 percent.
Examples 1 to 3, specific chemical components and weight percentages thereof of a low internal stress titanium-containing high strength steel are shown in table 1; comparative examples 1-2, chemical compositions and weight percentages thereof are also shown in table 1:
TABLE 1
Specific process data for the production process characteristics in examples 1-3 and comparative examples 1-2 are shown in Table 2:
TABLE 2
According to the national standards GB/T228 and GB/T231, the performances of the low internal stress high-strength steel in the test examples 1-3 and the comparative examples 1-2 are shown in Table 3.
TABLE 3
It can be seen that the tensile properties of the examples and the comparative examples are substantially at the same level, but the low temperature impact energy of the examples is relatively higher, which is related to lower internal stress and uniformity, and it can be seen from fig. 2 that the absolute value of the internal stress of the examples is smaller, the uniformity is higher, and the internal stress uniformity of the comparative examples is poorer. Fig. 1 is a schematic diagram of internal stress detection.
Although embodiments of the present invention have been shown and described above, it is understood that the above embodiments are exemplary and should not be construed as limiting the present invention, and that variations, modifications, substitutions and alterations can be made to the above embodiments by those of ordinary skill in the art within the scope of the present invention.
Claims (2)
1. The low-internal-stress titanium-containing high-strength steel is characterized by comprising the following chemical components in percentage by mass: c: 0.06% -0.11%, Si: 0.10-0.25%, Mn: 1.1-1.4%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Ti: 0.06% -0.10%, Nb: 0.010-0.030 percent, N is less than or equal to 0.005 percent, Als: 0.02% -0.05%, Mn/C: 13% -17%, Ti/Nb: 3.5 to 4.5 percent of Fe and impurities in balance; the production method comprises the following steps of (1),
adopting a blast furnace molten iron, molten iron desulphurization, converter smelting, LF + RH refining, continuous casting, hot charging and hot conveying, heating, rolling, laminar cooling, coiling, flattening and finishing, and heat treatment process route;
the technological parameters are as follows:
hot charging and hot conveying: after the continuous casting plate blank is off-line, the continuous casting plate blank is conveyed to the front of a heating furnace for slow cooling, and the hot charging temperature is more than 400 ℃;
heating: the tapping temperature is 1200-1250 ℃, and the heating time is more than or equal to 140 min;
rolling: two-stage controlled rolling is adopted, wherein the outlet temperature of rough rolling is 1020-1060 ℃, and the finish rolling temperature of finish rolling is 790-830 ℃;
laminar cooling: the variable cooling speed control is adopted, the cooling speed is started to be 20 ℃/s-30 ℃/s, the cooling speed is basically linearly reduced to be below 10 ℃/s along with the cooling process and the temperature of the steel coil is reduced, and the coiling temperature is 490-530 ℃;
leveling and finishing: opening and flattening, and packaging;
and (3) heat treatment: and (3) carrying out tempering heat treatment on the whole package, wherein the tempering temperature is 520-620 ℃, and the heat preservation time is (package thickness value + 60-80) min.
2. The low internal stress titanium-containing high strength steel according to claim 1, wherein the split flat finishing has a tundish thickness of 15mm to 50 mm.
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