CN101487096B - Low-alloy high-strength C-Mn-Al Q & P steel and method of manufacturing the same - Google Patents
Low-alloy high-strength C-Mn-Al Q & P steel and method of manufacturing the same Download PDFInfo
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Abstract
The invention relates to a low-alloyed and high-strength Q and amp of a C-Mn-Al system; P steel; and a manufacturing method thereof, which belong to the technical field of metal materials. The method comprises the following processing steps of: (1) smelting and cast blocking: the mass percentages of the components are as follows: 0.16 percent to 0.25 percent of C, less than or equal to 0.40 percent of Si, 1.20 percent to 1.60 percent of Mn, 1.0 percent to 1.5 percent of Al, less than or equal to 0.02 percent of P, less than or equal to 0.008 percent of S and the balance of ferrite. (2) rolling: after the multi-pass hot-rolling of rough rolling and finish rolling, wherein, the deformation of roughing pass is 10 percent to 30 percent, the total deformation of the finish rolling is more than60 percent, a hot rolled plate is subjected to multi-pass cold rolling, the deformation is 5 percent to 50 percent, and the plate is rolled to be a thin plate with the thickness being 0.6 to 2.0mm. (3) heat treating: firstly, austenitizing of 850 to 930 DEG C is carried out in a heating furnace, temperature is kept for 100 to 200 seconds and then rapid quenching is carried out to reach 230 to 250DEG C, the temperature is kept for 20 to 40 seconds, after that the temperature is kept in 300 to 400 DEG C for 120 to 3600 seconds, at last fast cooling is carried out to room temperature (the speedof the cooling is not less than 10 DEG C/s). The Q and amp and the P steel have economic components, good quality of the surface, high strength and good shaping resistance. The strength and ductilityproduct can reach over 37000MPa question mark percent.
Description
Technical field
The invention belongs to the metallic substance technical field, the C-Mn-Al that relates in particular to a kind of low-alloy high-strength is Q﹠amp; P steel and manufacture method thereof.
Background technology
Follow the high speed development of automotive industry and the raising of mankind itself's environmental consciousness, the requirement that improves fuel efficiency and strengthen vehicle safety strengthens day by day.For improving vehicle safety and alleviating car body weight, in recent years, the research of high-strength steel (HSS) becomes one of focus of ferrous materials research.Automobile structure adopts high tensile steel plate in a large number, manufacturing cost for high-strength vehicle structure iron in reducing, developed cheap, intensity is high and the steel grade that has excellent formability, as DP (Dual-Phase Steel) steel, be dual phase steel, TRIP (Transformation Induced Plasticity) steel, i.e. phase change induction plasticity steel.
The DP steel, a kind of microtexture is martensite+ferritic Hi-Stren steel, its technology of the dual phase steel that people such as the Zhang Hong of Baosteel develop (CN101270453A) mainly be heat cold rolling after, pot galvanize recrystallization annealing, annealing temperature is 800～860 ℃, cooling rate from annealing temperature to the zinc pond is 5～16 ℃/S, finish zinc-plated or Alloying Treatment after cooling rate greater than 7 ℃/S.Martensite content is at 10%-15%, and tensile strength is greater than 800MPa, yield strength 350～500MPa, and breaking elongation is greater than 12%.
The TRIP steel is to be prepared from by means of hot rolling or critical zone isothermal quenching thermal treatment process, and carbon atom can spread to austenite in the time of bainitic transformation, obtains containing the austenitic three-phase contexture of a large amount of stable residuals (ferrite+bainite+residual austenite).Wherein residual austenite has played the effect of TRIP effect.At the hot-rolled low-silicon multiphase steel (CN101058863A) of exploitations such as the grandson Zu Qing of University of Science ﹠ Technology, Beijing, after its technology was austenitizing, the hot rolling dependent variable behind the generation ferrite, was as cold as bainite phase region isothermal 10%～50% soon, and last water-cooled or air cooling are to room temperature.Its ferrite 40%～60%, bainite 30%～45%, residual austenite 8%～15%.
U.S. Ke Zhou ore deposit school Speer J.G has proposed Q﹠amp at first; P (Quenching and Partitioning) technology is produced steel grade by the volume fraction of the rich carbon retained austenite under the control room temperature.Q﹠amp; The P steel is a kind of martensitic steel in essence, but it is different from traditional tempered martensite steel, it with the tempered martensite steel under equality strength, plasticity significantly improves.This is because Q﹠amp; Have residual austenite in the tissue of P steel, this part austenite changes martensite in deformation process, produces the TRIP effect, has increased substantially the plasticity of steel.Its martensite content is about 70～80%, and residual austenite content is 15～20%.
High strength martensitic steel (CN101270453A) process Q-tempering in exploitations such as Iron and Steel Research Geueral Inst Huang Han though intensity is higher, can reach 1.2GPa, because matrix is mainly martensite, unit elongation is lower.
Work such as Speer show: 0.19C-1.59Mn-1.63Si is after 950 ℃ of complete austenitizings, again through Q﹠amp; P handles: 220 ℃ of insulation 3s and 350 ℃ of insulation 10s, and its yield strength reaches 1201MPa, and tensile strength reaches 1483MPa, even elongation after fracture 4.7%, total elongation after fracture 9.0%, residual austenite content is 2.6%; Through the annealing of 820 ℃ of insulation 180s two-phase regions, again through Q﹠amp; P handles, 200 ℃ of insulation 10s and 400 ℃ of insulation 10s', 0.2% yield strength is 781MPa, tensile strength is 1179MPa, and even elongation after fracture 9.9%, total elongation after fracture 12.8%, residual austenite content is 8.4%, austenite contains carbon concentration 1.2%.
Q﹠amp; The intensity of P steel is because the matrix ratio of martensite is big, and than DP, TRIP is all high, and because residual austenite is arranged, plasticity is better than martensitic steel, and strength and ductility product is better than DP and TRIP steel.Though higher for intensity in the result of study of Speer, plasticity is lower than the present invention, total strength and ductility product is lower than the present invention, and Si content is higher in its composition, and the hot rolling performance reduces, and reduces the wettability of steel plate in galvanizing process, plate surface quality is descended, and the workpiece plating is poor.The present invention proposes progressively partly to replace Si with Al, helps the raising of surface quality and the improvement of hot dip.
Summary of the invention
The object of the present invention is to provide a kind of Q﹠amp; P steel and production method thereof make it have high strength, high-ductility, and adopt Al to replace Si to reduce the content of Si, improve the hot dip of steel and improve surface quality.
Its Principles of Metallography are as follows:
Carbon: from strengthening mechanism, the most economical effective means of Fe-C alloy is the solution strengthening of carbon.In all elements, the effect that carbon reduces the Ms temperature is the strongest, is that austenitic transformation is that martensite strengthening is mutually indispensable.And if carbon content is when low, after the thermal treatment partition austenitic carbon content cross low at room temperature can not stable existence.But carbon content is too high in steel, and welding property descends, and more twins sub-structure appears in steel inevitably after quenching, might increase the tendency of quenching crack and diminish toughness.
Manganese: from the Fe-Mn equilibrium phase diagram as can be known, Fe and Mn dissolve each other when liquid.When Mn content was high, liquidus line and solidus curve were very approaching, almost overlapped.Mn is as the element that enlarges austenitic area (γ) in the Fe-C equilibrium phase diagram, and with the increase of Mn content, critical temperature A4 point raises, and A3 point descends, austenitic area expansion, and (α+γ) moves down into lower temperature in the while critical zone.Manganese and carbon can both make austenitic stability improve.Its effect mainly is to strengthen stabilization of austenite, prolongs it and changes incubation period, also impels Ms to reduce to below the room temperature simultaneously, forms the residual austenite of the rich carbon of certain volume.But Mn adds too much, causes the residual austenite volume to increase.Simultaneously, the probability that occurs white point in the smelting and the operation of rolling is increased, the trend of grain coarsening strengthens, and reduces the plasticity and the toughness of steel, and causes that welding property worsens.
Silicon: silicon mainly exists in the solid solution mode, can improve the intensity and the hardness of steel, and in the partition process, suppress the formation of cementite, make carbon further accumulate in the retained austenite, impel martensite to begin transition temperature Ms and reduce to below the room temperature, form the retained austenite of rich carbon.High-load silicon can form stable oxide, cuts off zinc liquid and surface of steel plate reaction in galvanization production line, reduces the wettability of steel plate, and plate surface quality is descended, and the workpiece plating is poor.
Aluminium: the deoxidizing capacity of aluminium is very strong, and deoxidation products is Al
2O
3, its fusing point is 2050 ℃.But owing to there are MnO, FeO, SiO in the steel
2Deng oxide compound, so Al
2O
3Be easy to combine formation low melting point, low-density inclusion, as MnOAl with them
2O
3(1560 ℃ of fusing points), Al
2O
3SiO
2(1487 ℃ of fusing points).This shows that aluminum oxide is difficult to form nucleus and the effect of playing thinning microstructure in crystallisation process.The crystalline structure of Al is similar to austenite, is face-centered cubic crystal, and its solid solution dwindles the austenite phase region in Fe strongly, forms γ and encloses mutually.Al can increase stacking fault energy, and suppresses γ to the ε transformation, can play the effect of stable austenite.The indissoluble particle that the small and dispersed that element such as Al and C, N forms distributes can play the effect of crystal grain thinning.In addition, Al can significantly improve tensile strength and unit elongation, suppresses separating out of cementite.With Al for Si as the auto sheet material, can improve surface quality problems, coating is better, strength and ductility product is higher, has high and stable work hardening exponent value.
Sulphur and phosphorus: sulphur forms plastic occluded foreignsubstance MnS with chemical combination such as manganese in steel, sulphur and phosphorus are especially unfavorable to the plasticity of steel, belong to impurity element, remove in smelting process as far as possible.
According to above Principles of Metallography and present process requirements, the present invention proposes a kind of high strength Q﹠amp; The P steel, its composition quality per-cent is: C 0.16～0.25, Si≤0.40, Mn 1.20～1.60, Al 1.0～1.5, P≤0.02, S≤0.008, all the other are iron and unavoidable impurities.
The invention allows for and make above-mentioned high strength Q﹠amp; The processing method of P steel comprises the steps:
(1) smelt: with vacuum induction furnace smelting, be cast as base,
(2) rolling: at first through roughing, the hot rolling of finish rolling multi-pass, Heating temperature is 1150 ℃, is incubated 40 minutes, and start rolling temperature is 1100 ℃, and finishing temperature is 850 ℃, adopts the technology of controlled rolling and controlled chilling in the operation of rolling.Wherein the roughing pass deformation is 10～30%, and the finish rolling total deformation is more than 60%.Again that hot-rolled sheet is cold rolling through multi-pass, pass deformation is 5～50%, and cold rolling total deformation is rolled into the thin plate that thickness is 0.6～2.0mm more than 60%;
3) thermal treatment.
Q﹠amp is taked in thermal treatment wherein; The P thermal treatment process is at Q﹠amp; In the P process heat treating processes, comprise austenitizing insulation, quenching obtains a certain proportion of martensite and retained austenite, carries out partition being heated to the partition temperature, is quenched to room temperature at last.Because the deposition of carbide can consume useful carbon in the heat treatment process, be disadvantageous to the rich carbon of retained austenite.Therefore, suppressing effectively that carbide separates out is the key of this technology controlling and process.Theoretical deduction shows: when the carbon geochemistry gesture in retained austenite and the martensite equated, partition technology finished.This will be avoided the cementite in the processing of partition postcooling to separate out, and partition is handled and improved austenitic stability greatly.Simultaneously in quenching process, quenching temperature is on the low side, and in heat tracing process subsequently, cementite or cementite separates out (being equivalent to quenching+average tempering) in the middle of may having, because separating out of cementite consumed useful carbon, the final austenite content that obtains seldom; Too high when quenching temperature, the test steel plate makes to test in the steel to guarantee that after art breading all austenites are rich in enough carbon and are stabilized to room temperature owing to contain more austenite after quenching.So the control quenching temperature is also extremely important.The thermal treatment process that the present invention takes is as follows: at first in process furnace through 850～930 ℃ of austenitizings and be incubated 100～200s, fast quenching to 230 behind the sample austenitizing～250 ℃ also are incubated 20～40s, subsequently 300～400 ℃ of insulations, soaking time is respectively 120～3600s, is not less than 10 ℃/s with speed of cooling at last and is quickly cooled to room temperature.
The superstrength auto sheet Q﹠amp that the present invention proposes; P steel and processing method thereof, the composition design is economical, and technology controlling and process is simple and easy to do.The intensity height of steel plate has high plasticity, and strength and ductility product can reach 37407MPa%.After mentioned component and technological process, the cold-reduced sheet tensile strength of thickness of slab 1.2mm can reach 1034MPa, and unit elongation A50 (JISS gauge length 50mm sample) can reach 37.9%.Tissue is mainly: martensite, residual austenite contain a little ferrite.
Description of drawings
Fig. 1. be thermal treatment process schematic diagram of the present invention
Fig. 2. be microtexture after the hot rolling of the embodiment of the invention 2
Fig. 3. be the cold rolling back microtexture of the embodiment of the invention 2
Fig. 4. be the scanning electron microscope tissue of the embodiment of the invention 2
Fig. 5. be the transmission electron microscope tissue of the embodiment of the invention 2
Embodiment
The present invention lists 12 embodiment altogether, and wherein the concrete chemical ingredients of the employed steel of each embodiment is as shown in table 1.All embodiment all adopt same hot rolling and cold-rolling process, be that hot rolling comprises 5 passage roughing (R1-R5) and 5 passage finish rolling (F1-F5), concrete hot rolling technology is as shown in table 2, take 7 passages cold rolling (C1-C7), cold-rolling process is as shown in table 3, take different thermal treatment process, thermal treatment process is as shown in table 4, and the mechanical property of the steel of each embodiment that finally obtains is as shown in table 5.
Table 1 Q﹠amp of the present invention; The chemical ingredients of P steel (weight percent %)
| Embodiment | C | Si | Mn | Al | P | S | Fe |
| 1 | 0.16 | 0.21 | 1.22 | 1.43 | 0.008 | 0.007 | Surplus |
| 2 | 0.18 | 0.39 | 1.47 | 1.30 | 0.006 | 0.006 | Surplus |
| 3 | 0.18 | 0.39 | 1.47 | 1.30 | 0.006 | 0.006 | Surplus |
| 4 | 0.21 | 0.18 | 1.32 | 1.49 | 0.008 | 0.006 | Surplus |
| 5 | 0.21 | 0.18 | 1.32 | 1.49 | 0.008 | 0.006 | Surplus |
| 6 | 0.21 | 0.18 | 1.32 | 1.49 | 0.008 | 0.006 | Surplus |
| 7 | 0.21 | 0.40 | 1.37 | 1.29 | 0.007 | 0.006 | Surplus |
| 8 | 0.21 | 0.40 | 1.37 | 1.29 | 0.007 | 0.006 | Surplus |
| 9 | 0.21 | 0.40 | 1.37 | 1.29 | 0.007 | 0.006 | Surplus |
| 10 | 0.25 | 0.18 | 1.50 | 1.46 | 0.006 | 0.006 | Surplus |
| 11 | 0.25 | 0.18 | 1.50 | 1.46 | 0.006 | 0.006 | Surplus |
| 12 | 0.25 | 0.38 | 1.60 | 1.34 | 0.008 | 0.006 | Surplus |
Table 2 Q﹠amp of the present invention; The hot rolling technology of P steel
| Passage | Rolling sequence | Absolute deformation amount Δ h/mm | Relative deformation ε/% | Outgoing gauge H/mm | Rolling temperature/℃ |
| R1 | Roughing | 9.5 | 11.9 | 70.5 | 1185 |
| R2 | Roughing | 14.0 | 19.9 | 56.5 | 1171 |
| R3 | Roughing | 16.0 | 28.3 | 40.5 | 1152 |
| R4 | Roughing | 12.5 | 29.6 | 28.0 | 1127 |
| R5 | Roughing | 8.0 | 28.6 | 20.0 | 1095 |
| F1 | Finish rolling | 7.5 | 37.5 | 12.5 | 1060 |
| Passage | Rolling sequence | Absolute deformation amount Δ h/mm | Relative deformation ε/% | Outgoing gauge H/mm | Rolling temperature/℃ |
| F2 | Finish rolling | 4.5 | 36.0 | 8.0 | 969 |
| F3 | Finish rolling | 2.5 | 31.3 | 5.5 | 931 |
| F4 | Finish rolling | 1.5 | 23.6 | 4.2 | 899 |
| F5 | Finish rolling | 0.5 | 11.1 | 3.5 | 871 |
Table 3 Q﹠amp of the present invention; The cold-rolling process of P steel
| Passage | Absolute deformation amount Δ h/mm | Relative deformation ε/% | Outgoing gauge h/mm |
| C1 | 0.5 | 14.3 | 3 |
| C2 | 0.5 | 16.7 | 2.5 |
| C3 | 0.4 | 16 | 2.1 |
| C4 | 0.3 | 14.3 | 1.8 |
| C5 | 0.2 | 12.5 | 1.6 |
| C6 | 0.2 | 12.5 | 1.4 |
| C7 | 0.2 | 14.3 | 1.2 |
Table 4 Q﹠amp of the present invention; P Heat Treatment Of Steel technology
| Embodiment | Austenitizing temperature TA/ ℃ | Austenitizing time/s | Quenching temperature TQ/ ℃ | Quenching Soaking Time/s | P/ ℃ of partition temperature T | Partition time/s | Final cooling temperature/℃ |
| 1 | 850 | 100 | 238 | 20 | 300 | 1200 | 15 |
| 2 | 860 | 150 | 233 | 30 | 320 | 1200 | 15 |
| 3 | 910 | 200 | 242 | 40 | 350 | 3600 | 25 |
| 4 | 870 | 120 | 250 | 24 | 320 | 120 | 20 |
| Embodiment | Austenitizing temperature TA/ ℃ | Austenitizing time/s | Quenching temperature TQ/ ℃ | Quenching Soaking Time/s | P/ ℃ of partition temperature T | Partition time/s | Final cooling temperature/℃ |
| 5 | 910 | 200 | 233 | 40 | 350 | 960 | 25 |
| 6 | 930 | 200 | 250 | 40 | 400 | 2400 | 30 |
| 7 | 860 | 150 | 239 | 30 | 320 | 120 | 10 |
| 8 | 900 | 200 | 240 | 40 | 350 | 960 | 15 |
| 9 | 930 | 160 | 245 | 32 | 400 | 2400 | 30 |
| 10 | 880 | 100 | 231 | 20 | 300 | 120 | 20 |
| 11 | 920 | 150 | 239 | 30 | 320 | 300 | 30 |
| 12 | 900 | 200 | 243 | 40 | 320 | 300 | 10 |
The mechanical property of table 5 embodiment of the invention
| Embodiment | Rm/MPa | A50/％ | Rm×A50/MPa·％ |
| 1 | 885 | 21.7 | 19204.5 |
| 2 | 1050 | 23.6 | 24780 |
| 3 | 960 | 36.9 | 35424 |
| 4 | 1008 | 22.4 | 22579.2 |
| 5 | 1034 | 24.7 | 25539.8 |
| 6 | 987 | 37.9 | 37407.3 |
| 7 | 894 | 20.2 | 18058.8 |
| 8 | 997 | 24.2 | 24127.4 |
| 9 | 978 | 32.1 | 31393.8 |
| 10 | 880 | 26.2 | 23056 |
| Embodiment | Rm/MPa | A50/％ | Rm×A50/MPa·％ |
| 11 | 890 | 29.1 | 25899 |
| 12 | 886 | 31.2 | 27643.2 |
By table 5 as seen, the Q﹠amp of the present invention's proposition; The P steel has high strength, high-ductility, and tensile strength is all greater than 886MPa, and unit elongation A50 is greater than 20.2%, up 37.9%, strength and ductility product up 37407MPa%.
The microtexture of embodiment 2 is analyzed as can be known Q﹠amp after the hot rolling; The P steel be organized as equiaxial ferrite+pearlitic structure (as Fig. 2), the ferrite+pearlite transformation that the axle shape such as is after cold rolling is the extended distressed structure, as shown in Figure 3.Through Q﹠amp; After the P thermal treatment process, adopt scanning electron microscope that heterogeneous microstructure is observed discovery, mainly present martensitic stucture (as Fig. 4) in the matrix,, need to observe by the TEM Electronic Speculum owing under scanning electron microscope, can not clearly differentiate retained austenite.Its delicate tissues structure as shown in Figure 5, through quench and the partition processing after the test steel present typical lath martensite tissue, and the substructure of lath is a high density dislocation.Organizing mainly is two phase composites of arranging by alternately, is the membranaceous retained austenite that is organized as therebetween.
Claims (3)
1. C-Mn-Al series high strength Q﹠amp; The P steel is characterized in that the composition quality per-cent of steel is:
C：0.16～0.25、Si：≤0.40、Mn：1.201.60、Al：1.0～1.5、
P :≤0.02, S :≤0.008, all the other are iron.
2. C-Mn-Al series high strength Q﹠amp as claimed in claim 1; The manufacture method of P steel, its feature comprises the steps:
1) smelt, be cast as base by the composition of claim 1:
2) rolling: through roughing, the hot rolling of finish rolling multi-pass, the roughing pass deformation is 10～30%, and the finish rolling total deformation is more than 60%, again that hot-rolled sheet is cold rolling through multi-pass, pass deformation is 5～50%, and cold rolling total deformation is more than 60%, is rolled into the thin plate that thickness is 0.6～2.0mm;
3) thermal treatment.
3. C-Mn-Al series high strength Q﹠amp as claimed in claim 2; The manufacture method of P steel is characterized in that, Q﹠amp is adopted in the thermal treatment in the step 3); The P thermal treatment process, at first in process furnace through 850～930 ℃ of austenitizings and be incubated 100～200s, fast quenching to 230 behind the thin plate austenitizing～250 ℃ also are incubated 20～40s, subsequently 300～400 ℃ of insulations, soaking time is respectively 120～3600s, is not less than 10 ℃/s with speed of cooling at last and is quickly cooled to room temperature.
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| CN110412067A (en) * | 2019-08-16 | 2019-11-05 | 武汉钢铁有限公司 | A kind of thermal modeling test determines the test method of austempering temperature |
| CN111321281B (en) * | 2020-04-21 | 2021-12-07 | 山东钢铁集团日照有限公司 | Method for realizing reinforcement and plasticization of I & QP steel through microstructure regulation |
| CN113061810B (en) * | 2021-03-17 | 2022-05-17 | 山东钢铁集团日照有限公司 | Production method of 590 MPa-grade enhanced formability hot-dip galvanized dual-phase steel |
| CN114540600B (en) * | 2022-01-17 | 2022-11-08 | 苏州大学 | Preparation method for increasing austenite content and stability of medium manganese steel |
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