CN108277434A - The precipitation enhancement type ferritic steel and production method that a kind of yield strength is 900MPa grades - Google Patents
The precipitation enhancement type ferritic steel and production method that a kind of yield strength is 900MPa grades Download PDFInfo
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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
-
- 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
- C21D1/26—Methods of annealing
-
- 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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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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
-
- 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
- C21D8/0231—Warm rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
A kind of precipitation enhancement type ferritic steel that yield strength is 900MPa grades, component and wt% are：C：0.105 ~ 0.139%, Si：0.05 ~ 0.16%, Mn：0.59 ~ 0.98%, P：≤ 0.008%, S：≤ 0.003%, Cr：0.11 ~ 0.23%, Nb：0.121 ~ 0.182%, Ti：0.119 ~ 0.177%, Mo：0.22 ~ 0.47%, N：≤0.005%.Production method：Through it is conventional smelt, be cast into base after to heating strand；Two-part hot rolling；Section cooling；It batches；Pickling after cooled to room temperature；Warm-rolling；Annealing；It is cooling.The present invention can make the yield strength of steel in 903 ~ 946MPa, tensile strength can also make its elongation percentage >=21% in 952 ~ 987MPa, and ferrite average grain size is at 1.9 ~ 2.4 μm, precipitation strength contribution amount is 287 ~ 323MPa, has excellent plasticity, processability, welding performance.
Description
Technical field
The present invention relates to a kind of low-carbon superhigh intensity ferritic steel and its production method, definitely belonging to yield strength is
900MPa grades of precipitation strength type Ultra-fine Grained Ferrite Steel and production method, it is suitable for automobile, communications and transportation, engineering machinery etc.
Field.
Background technology
In recent years, high-performing car is quickly grown with steel, is considered as the key of automotive light weight technology, is to realize vehicle energy saving
One of the important means of emission reduction.Put forth effort development of the research and development high-performing car steel technology to China's steel and automobile industry
It is of great significance.An important development direction of the superhigh intensity ferritic steel as high-performing car steel has excellent
Plasticity, processability, welding performance etc. are especially suitable for making the auto parts and components of labyrinth, and simple production process, cost
It is low.However, ferritic steel intensity is relatively low, how to improve its intensity becomes the key of development superhigh intensity ferrite automobile steel.
Currently, super-high strength steel, mainly based on martensite steel and bainitic steel, this kind of steel has superhigh intensity but its elongation percentage is relatively low, nothing
Method meets the requirement for the auto parts and components for making labyrinth.In addition, the production of such steel need to add a large amount of alloying element,
And it needs by complicated heat treatment process, manufacturing process is long, and production cost is high, as through retrieval：
The document that Chinese Patent Application No. is 201410535894.4, it discloses a kind of 800MPa grades of cold-rolled biphase steel and its lifes
Production method, composition range are：C0.14~0.17%, Si0.45~0.55, Mn1.6~1.8, Cr0.55~0.65%, P≤
0.016%, S≤0.008%, Als0.02~0.05%, N≤0.004%, surplus Fe.Pass through smelting, hot rolling, cold-rolling continuous annealing work
Skill, it is 800~850MPa to have produced tensile strength, and yield strength is 450~550MPa, and elongation percentage is 15~17%, metallographic group
It is woven to the cold-rolled biphase steel of ferrite+martensite.Its main strengthening mechanism is the phase transformation strengthening of martensite, and intensity is high but it extends
Rate is relatively low.It is difficult to meet the requirement of labyrinth auto parts and components.
The document that Chinese Patent Application No. is 201210117567.8, it discloses a kind of yield strengths to be higher than 900MPa
Micro Alloying state hot-strip and preparation method thereof, use the low-carbon composition design, composition range to be：C0.06 ~ 0.12%,
Si0.10 ~ 0.30%, Mn0.80 ~ 1.20%, Nb0.00 ~ 0.04%, V0.00 ~ 0.04%, Ti0.02 ~ 0.10%, Cr0.8 ~ 1.20%,
Mo0.10 ~ 0.30%, B0.001 ~ 0.003%, P ＜ 0.012%, S ＜ 0.01%, by adding microalloy element and controlled rolling and controlled cooling, control
It rolls and controls cold+tempering technology, produce yield strength and be not less than 900MPa, tensile strength is not less than 940MPa, and elongation after fracture is
12 ~ 16% steel band, metallographic structure be the comparatively fine bainite/martensite or tempering bainite/tempered martensite of crystal grain and
The tissue of a small amount of retained austenite.Though its yield strength has reached 900MPa grades, its elongation percentage is only 12 ~ 16%, main strong
Change the phase transformation strengthening that mechanism is bainite/martensite, intensity is high but its elongation percentage is relatively low.Higher level portion cannot still be met
The requirement of part.
The document that Chinese Patent Application No. is 201610713632.1, it discloses a kind of resisting with sheet billet Direct Rolling
The thin hot forming steel of tensile strength >=1100MPa and production method, composition range are：C：0.12~0.16%, Si：0.15~
0.20%, Mn：0.7~1.0%, P≤0.02%, S≤0.008%, Als：0.015~0.060%, Cr：0.15~0.20%, Ti：
0.005~0.02% or Nb：0 .005~0.02% or V：0.005~0.02% or in which the two or more mixing with arbitrary proportion,
B：0.0005~0.0020%, N≤0.005%.It uses the hot rolling raw material that thin slab continuous casting and rolling produces, and carries out heating austenite
Change；Mould punching forming is recycled, quenching treatment is then carried out, finally obtains tensile strength >=1100MPa hot forming steel, prolong
Stretch rate and be no more than 9%, quenched finished product is organized as martensite, relies primarily on martensitic traoformation reinforcing, so intensity it is high but its
Elongation percentage is relatively low.
However, existing ferritic steel can be met the requirements for elongation percentage, but its intensity is relatively low, at present ferritic steel
Yield strength be generally less than 700MPa.The intensity rank of ferritic steel how is improved, then becomes development superhigh intensity iron element
The key of body steel.Ferritic steel has excellent plasticity, processability, welding performance etc., is especially suitable for making labyrinth
Auto parts and components, and it is simple production process, at low cost.Superhigh intensity ferritic steel is an important hair of high-performing car steel
Open up direction.
And the present invention mainly uses Ti-Nb-Mo combined microalloying technologies, using the side of conventional hot rolling+warm-rolling+annealing
Formula obtains a kind of yield strength ranging from 903 ~ 946MPa, tensile strength ranging from 952 ~ 987MPa, elongation percentage ranging from 21.2
~ 23.4%, ferrite average grain size is 1.9 ~ 2.4 μm, and the precipitation strength type that precipitation strength contribution amount is 287 ~ 323MPa is super
Fine ferrite grain steel.The present invention's is mainly characterized by conjunction with hot rolling, warm-rolling and annealing process, in fining ferrite grains size
Precipitation enhancement is given full play to simultaneously, realizes that the superelevation of ferritic steel is strengthened.
Invention content
It is insufficient the invention reside in overcoming existing for existing ferritic steel, provide a kind of yield strength that can make steel 903 ~
946MPa, tensile strength can also make its elongation percentage >=21% in 952 ~ 987MPa, and ferrite average grain size is 1.9 ~ 2.4
μm, precipitation strength contribution amount is 287 ~ 323MPa, the precipitation strength type with excellent plasticity, processability, welding performance etc.
Ferritic steel and production method.
Realize the measure of above-mentioned purpose：
A kind of precipitation enhancement type ferritic steel that yield strength is 900MPa grades, component and weight percent content are：C：
0.105 ~ 0.139%, Si：0.05 ~ 0.16%, Mn：0.59 ~ 0.98%, P：≤ 0.008%, S：≤ 0.003%, Cr：0.11 ~ 0.23%,
Nb：0.121 ~ 0.182%, Ti：0.119 ~ 0.177%, Mo：0.22 ~ 0.47%, N：≤ 0.005%, remaining is for Fe and inevitably
Impurity；Metallographic structure is pure ferrite；Mechanical property：Yield strength ranging from 903 ~ 946MPa, tensile strength ranging from 952 ~
987MPa, elongation percentage ranging from 21.2 ~ 23.4%；Ferrite average grain size is 1.9 ~ 2.4 μm.
Preferably：The weight percent content of C is 0.113 ~ 0.136%.
Preferably：The weight percent content of Mn is 0.66 ~ 0.95%.
Preferably：The weight percent content of Cr is 0.12 ~ 0.19%.
Preferably：The weight percent content of Nb is 0.131 ~ 0.166%.
Preferably：The weight percent content of Ti is 0.132 ~ 0.163%.
Preferably：The weight percent content of Mo is 0.25 ~ 0.45%.
Produce a kind of method for the precipitation enhancement type ferritic steel that yield strength is 900MPa grades, step：
1）Through it is conventional smelt, be cast into base after to heating strand, it is heated after strand temperature control at 1281 ~ 1307 DEG C, add
The hot time is in 93 ~ 118min；
2）Carry out two-part hot rolling：Wherein, control roughing end temp adds up reduction ratio 82 ~ 87% at 1078 ~ 1092 DEG C；
Finish rolling finishing temperature is controlled at 822 ~ 839 DEG C, adds up reduction ratio 92 ~ 95%；
3）Section cooling is carried out, coiling temperature is cooled in the case where cooling velocity is 55 ~ 63 DEG C/s；
4）It is batched, control coiling temperature is at 563 ~ 582 DEG C；
5）Conventional acid is carried out after cooled to room temperature to wash；
6）Warm-rolling is carried out, control warm-rolling temperature adds up reduction ratio 63 ~ 79% at 123 ~ 237 DEG C；
7）Anneal under perhydro atmosphere protection, annealing temperature control at 550 ~ 597 DEG C, and at this temperature heat preservation 30 ~
40min；
8）It is cooled down, is cooled to room temperature in the case where cooling velocity is not less than 82 DEG C/s.
Preferably：The warm-rolling temperature adds up reduction ratio 66 ~ 73% at 136 ~ 227 DEG C.
Preferably：The annealing temperature is at 560 ~ 589 DEG C, and soaking time is in 32 ~ 37min.
Effect and the mechanism of main intensified element and technique in the present invention
C：Select low-carbon design the purpose is to reduce the quantity of cementite in steel microscopic structure, inhibit the formation of pearlite.When C contains
It is difficult to form nanoscale precipitate with combinations such as microalloy element Nb, Ti when carbon content is too low when amount is less than 0.105%, to difficult
To play the role of precipitation strength.When C content is more than 0.139%, welding and low-temperature flexibility can drastically deteriorate, therefore by C content
Control is within the scope of 0.1,05 ~ 0.139%, and preferably the weight percent content of C is 0.113 ~ 0.136%.
Si：Playing the role of solution strengthening in steel, while being deoxidant element, Si contents should control 0.05% or more, but
When Si contents are more than 0.16%, the formation of interior rusty scale can be promoted, de-scaling when rolling can be given to bring difficulty, so as to cause steel band table
Face deterioration in addition, Si too high levels can also reduce the welding performance of steel, therefore is controlled 0.05 ~ 0.16%.
Mn：It is Strengthening and Toughening element important in steel, improves the manganese content in steel, the areas γ can be expanded, reduce transition temperature, expands
Big rolling range, promotes crystal grain refinement, and to increase the obdurability of steel, impact transition temperature also hardly happens variation, because
This Mn content should be greater than 0.59%, in addition, when Mn contents are higher than 0.98%, casting process easy tos produce strand crackle, simultaneously also
The welding performance of steel can be reduced, therefore by the control of Mn contents 0.59 ~ 0.98%, the preferably weight percent content of Mn is
0.66~0.95%。
P：P in steel can deteriorate the toughness of steel, especially tempestuously reduce the low-temperature impact toughness of steel, therefore by P content
Control is below 0.008%.
S：The MnS that S too high levels generate in steel, which is mingled with, can make the vertically and horizontally performance of steel generate notable difference, and impaired low temperature is tough
Property.S contents should control below 0.003%.
Cr：The intensity and hardness of steel can be improved in Cr elements in steel, and therefore, Cr contents are controlled 0.12% or more, are in addition examined
Consider the economy of ingredient, therefore by the control of Cr contents in 0.11 ~ 0.23% range, the preferably weight percent content of Cr is
0.12~0.19%。
Nb：It is strong carbonitride-forming elements, micro Nb can inhibit the recrystallization of deformed austenite in steel, prevent austenite
Crystal grain is grown up, and austenite recrystallization temperature is improved, and crystal grain thinning improves the intensity and toughness of steel.In addition, in cooling procedure
The precipitation of Nb (CN), can play the role of precipitation strength, improve the mechanical performance of steel, consider Nb with coherent element in Ovshinsky
The constituent contents such as Ti, N, S, C in solubility product and steel in body and ferrite, thus by the control range of Nb contents be 0.12 ~
0.18%, if being less than 0.12%, Nb can be caused to be difficult to play refined crystalline strengthening and precipitation strength effect, if being higher than 0.18%, can led
It causes Nb elements not to be dissolved completely, unnecessary alloying element is caused to lose.Preferably the weight percent content of Nb is 0.131
~0.166%。
Ti：It is strong carbonitride-forming elements, when Ti contents are less, Ti preferentially can be combined to form TiN with N, TiN particles
It is relatively large sized, it will not all be dissolved under the hot conditions for heating and welding, hence it is evident that the welding performance of steel is improved, in addition, TiN
Can also effectively pin austenite grain boundary, help that austenite grain is prevented to grow up, when Ti contents are more, in addition to TiN can be formed
Outside, remaining Ti can be combined to form the smaller TiC particles of size with the C in steel in steel, can play the role of precipitation strength, in steel
Ti contents are too low, Ti can be caused to be difficult to play refined crystalline strengthening and precipitation strength effect, Ti too high levels can cause Ti elements can not
Solid solution completely causes unnecessary alloying element to lose.Consider Ti with coherent element consolidating in austenite and ferrite
The constituent contents such as Nb, N, S, C in solubility product and steel, therefore Ti contents are controlled in 0.119 ~ 0.177%, the preferably weight of Ti
Degree is 0.132 ~ 0.163%.
Mo：It is strong carbonitride-forming elements, Mo contents appropriate can prevent growing up for austenite grain, can improve conjunction
The intensity of Jin Gang at normal temperatures, while Mo can improve precipitation particles in the thermal stability in roughening stage, can effectively inhibit
The roughening of growing up of Second Phase Precipitation object particle granules, to improve the precipitation strength effect of experiment steel, therefore Mo contents should be greater than
0.22%, since Mo is precious metal, the considerations of for production cost, Mo contents are controlled in 0.22 ~ 0.47%, the preferably weight of Mo
It is 0.25 ~ 0.45% to measure degree.
N：Nitrogen in steel can at high temperature be combined with elements such as Ti, Nb forms corresponding compound, and this kind of compound is in height
It can be roughened under temperature, grow up, this seriously damages the plasticity and toughness of steel.In addition, this kind of coarse carbonitride formed at high temperature
Particle is smaller to precipitation strength contribution, and can consume the content of effective Ti, Nb in steel, therefore its content is controlled 0.005%
Below.
Why the present invention controls warm-rolling temperature at 123 ~ 237 DEG C, adds up reduction ratio 63 ~ 79%, is due to general
Warm-rolling is only applicable to this kind of steel grade being difficult to directly in cold rolling at room temperature of high-carbon, high-alloy steel, to improve this kind of steel cold-rolled
The processing hardening of journey improves machinability of this kind of steel in cold-rolled process.And the main purpose of warm-rolling technique described in this patent
It is the further fining ferrite grains size under suitable rolling temperature, improves refined crystalline strengthening effect.Warm-rolling temperature is higher than
237 DEG C, ferrite can be caused to recrystallize, cause crystallite dimension excessive, so as to cause refined crystalline strengthening decreased effectiveness.In addition,
Warm-rolling temperature is excessively high to also result in the second phase particles roughening generated in course of hot rolling, and leads to the decrease of precipitation strength effect.
When warm-rolling temperature is more than 79% less than 123 DEG C, accumulative deflection, operation of rolling resistance of deformation can be caused larger and be difficult to roll.It is tired
When counting deflection less than 63%, accumulative deflection is too small, ferrite grain size can be caused to be difficult to further refine, it may be difficult to obtain
Obtain the ferrite of ultra-fine grain；Preferably warm-rolling temperature adds up reduction ratio 66 ~ 73% at 136 ~ 227 DEG C.
Why the present invention controls annealing temperature at 550 ~ 597 DEG C, and keeps the temperature 30 ~ 40min at this temperature；Preferably
For annealing temperature at 560 ~ 589 DEG C, soaking time is since annealing temperature is higher than 597 DEG C, and soaking time is more than in 32 ~ 37min
At 40 minutes, second phase particles can be caused to grow up roughening, to make precipitation strength decreased effectiveness, annealing temperature such as be less than
550 DEG C, soaking time is less than 30 minutes, and second phase particles precipitation thermodynamics and kinetics condition can be made poor, lead to the second phase
Particle is difficult to be precipitated, to weaken precipitation strength effect.When cooling velocity after annealing is less than 82 DEG C/s, the second phase can be caused
Particle is grown up roughening in cooling procedure, to weaken precipitation strength effect.It therefore, should be to be not less than 82 DEG C/s's after annealing
Cooling velocity is cooled to room temperature.
The present invention is by mainly using Ti-Nb-Mo combined microalloyings, then the side using conventional hot rolling+warm-rolling+annealing
Formula, solves due to the excessively high difficulty for being difficult to direct cold rolling of steel hot rolling intensity, by the setting of rational temperature and deflection,
Ferrite grain size has fully been refined, the ferritic steel that average grain size is 1.9 ~ 2.4 μm of ultra-fine grains has been obtained, breaks through
The limiting value of 3.0 μm of the ferritic steel average grain size of produced in conventional processes.So that its yield strength of the steel plate of the present invention
Range is 952 ~ 987MPa in 903 ~ 946MPa, tensile strength, and 21.2 ~ 23.4%, ferrite average grain size exists elongation percentage
1.9 ~ 2.4 μm, precipitation strength contribution amount is the precipitation strength type Ultra-fine Grained Ferrite Steel of 287 ~ 323MPa.In addition, by reasonable
Hot rolling, warm-rolling and annealing process formulation make tiny, disperse the second phase grain while abundant fining ferrite grains
Sub to be fully precipitated, precipitation strength contribution amount is 287 ~ 323MPa, breaches conventional Ti-Nb composite micro-alloyed steel precipitation strength tributes
The limiting value of the amount of offering 250MPa, the superelevation for realizing ferritic steel are strengthened.Using steel plate produced by the invention with high intensity
While also have preferable plasticity.
Description of the drawings
Fig. 1 is the metallographic structure figure of the embodiment of the present invention；
Fig. 2 is the precipitate shape appearance figure of the embodiment of the present invention.
Specific implementation mode
The present invention is described in detail below：
Table 1 is the chemical composition list of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example；
Table 3 is the performance test results list of various embodiments of the present invention and comparative example.
Various embodiments of the present invention follow the steps below production：
1）Through it is conventional smelt, be cast into base after to heating strand, it is heated after strand temperature control at 1281 ~ 1307 DEG C, add
The hot time is in 93 ~ 118min；
2）Carry out two-part hot rolling：Wherein, control roughing end temp adds up reduction ratio 82 ~ 87% at 1078 ~ 1092 DEG C；
Finish rolling finishing temperature is controlled at 822 ~ 839 DEG C, adds up reduction ratio 92 ~ 95%；
3）Section cooling is carried out, coiling temperature is cooled in the case where cooling velocity is 55 ~ 63 DEG C/s；
4）It is batched, control coiling temperature is at 563 ~ 582 DEG C；
5）Conventional acid is carried out after cooled to room temperature to wash；
6）Warm-rolling is carried out, control warm-rolling temperature adds up reduction ratio 63 ~ 79% at 123 ~ 237 DEG C；
7）Anneal under perhydro atmosphere protection, annealing temperature control at 550 ~ 597 DEG C, and at this temperature heat preservation 30 ~
40min；
8）It is cooled down, is cooled to room temperature in the case where cooling velocity is not less than 82 DEG C/s.
1 various embodiments of the present invention of table and comparative example chemical composition list（wt%）
| Embodiment | C | Si | Mn | Ti | Mo | Nb | N | Cr | S | P |
| 1 | 0.127 | 0.08 | 0.98 | 0.152 | 0.22 | 0.182 | 0.003 | 0.13 | 0.003 | 0.007 |
| 2 | 0.139 | 0.13 | 0.72 | 0.119 | 0.46 | 0.127 | 0.005 | 0.11 | 0.002 | 0.008 |
| 3 | 0.109 | 0.16 | 0.61 | 0.169 | 0.24 | 0.171 | 0.004 | 0.15 | 0.001 | 0.005 |
| 4 | 0.113 | 0.10 | 0.95 | 0.163 | 0.45 | 0.166 | 0.005 | 0.19 | 0.003 | 0.008 |
| 5 | 0.126 | 0.06 | 0.81 | 0.158 | 0.42 | 0.157 | 0.002 | 0.12 | 0.002 | 0.004 |
| 6 | 0.121 | 0.05 | 0.86 | 0.123 | 0.27 | 0.172 | 0.003 | 0.22 | 0.003 | 0.002 |
| 7 | 0.136 | 0.07 | 0.66 | 0.132 | 0.31 | 0.131 | 0.001 | 0.15 | 0.003 | 0.006 |
| 8 | 0.119 | 0.11 | 0.75 | 0.145 | 0.25 | 0.143 | 0.004 | 0.17 | 0.002 | 0.004 |
| 9 | 0.112 | 0.09 | 0.63 | 0.177 | 0.36 | 0.129 | 0.002 | 0.21 | 0.001 | 0.005 |
| 10 | 0.105 | 0.15 | 0.59 | 0.166 | 0.47 | 0.121 | 0.005 | 0.23 | 0.002 | 0.006 |
| Comparative example 1 | 0.052 | 0.03 | 0.51 | 0.032 | 0.01 | 0.02 | 0.010 | 0.45 | 0.051 | 0.012 |
| Comparative example 2 | 0.221 | 0.24 | 1.06 | 0.012 | 0.03 | 0.06 | 0.043 | 0.01 | 0.011 | 0.029 |
| Comparative example 3 | 0.315 | 0.35 | 1.51 | 0.002 | 0.63 | 0.03 | 0.031 | 0.28 | 0.016 | 0.015 |
2 various embodiments of the present invention of table and comparative example technique major parameter list
3 various embodiments of the present invention of table and comparative example mechanics properties testing situation list
From table 3 it can be seen that steel plate yield strength ranging from 903 ~ 946MPa of institute's case study on implementation, tensile strength ranging from 952 ~
987MPa, elongation percentage ranging from 21.2 ~ 23.4%, ferrite average grain size are 1.9 ~ 2.4 μm, and precipitation strength contribution amount is
287 ~ 323MPa, 180 ° of cold-bending properties are qualified, and the yield strength range of comparative sample is only 321 ~ 532MPa, tensile strength model
Only 407 ~ 573MPa is enclosed, elongation percentage range is only 8.4 ~ 10.1%, and ferrite average grain size is 13.6 ~ 16.8 μm, precipitation
It is only 37 ~ 62MPa to strengthen contribution amount, and 180 ° of cold-bending properties are unqualified.It can be seen that the properties of embodiment described in this patent refer to
Mark is superior to comparative example.
Present embodiment is only the best example, not to the restricted implementation of technical solution of the present invention.
Claims (10)
1. the precipitation enhancement type ferritic steel that a kind of yield strength is 900MPa grades, component and weight percent content are：C：
0.105 ~ 0.139%, Si：0.05 ~ 0.16%, Mn：0.59 ~ 0.98%, P：≤ 0.008%, S：≤ 0.003%, Cr：0.11 ~ 0.23%,
Nb：0.121 ~ 0.182%, Ti：0.119 ~ 0.177%, Mo：0.22 ~ 0.47%, N：≤ 0.005%, remaining is for Fe and inevitably
Impurity；Metallographic structure is pure ferrite；Mechanical property：Yield strength ranging from 903 ~ 946MPa, tensile strength ranging from 952 ~
987MPa, elongation percentage ranging from 21.2 ~ 23.4%；Ferrite average grain size is 1.9 ~ 2.4 μm.
2. the precipitation enhancement type ferritic steel that a kind of yield strength as described in claim 1 is 900MPa grades, it is characterised in that：
The weight percent content of C is 0.113 ~ 0.136%.
3. the precipitation enhancement type ferritic steel that a kind of yield strength as described in claim 1 is 900MPa grades, it is characterised in that：
The weight percent content of Mn is 0.66 ~ 0.95%.
4. the precipitation enhancement type ferritic steel that a kind of yield strength as described in claim 1 is 900MPa grades, it is characterised in that：
The weight percent content of Cr is 0.12 ~ 0.19%.
5. the precipitation enhancement type ferritic steel that a kind of yield strength as described in claim 1 is 900MPa grades, it is characterised in that：
The weight percent content of Nb is 0.131 ~ 0.166%.
6. the precipitation enhancement type ferritic steel that a kind of yield strength as described in claim 1 is 900MPa grades, it is characterised in that：
The weight percent content of Ti is 0.132 ~ 0.163%.
7. the precipitation enhancement type ferritic steel that a kind of yield strength as described in claim 1 is 900MPa grades, it is characterised in that：
The weight percent content of Mo is 0.25 ~ 0.45%.
8. a kind of production method for the precipitation enhancement type ferritic steel that yield strength is 900MPa grades as described in claim 1,
Its step：
1）Through it is conventional smelt, be cast into base after to heating strand, it is heated after strand temperature control at 1281 ~ 1307 DEG C, add
The hot time is in 93 ~ 118min；
2）Carry out two-part hot rolling：Wherein, control roughing end temp adds up reduction ratio 82 ~ 87% at 1078 ~ 1092 DEG C；
Finish rolling finishing temperature is controlled at 822 ~ 839 DEG C, adds up reduction ratio 92 ~ 95%；
3）Section cooling is carried out, coiling temperature is cooled in the case where cooling velocity is 55 ~ 63 DEG C/s；
4）It is batched, control coiling temperature is at 563 ~ 582 DEG C；
5）Conventional acid is carried out after cooled to room temperature to wash；
6）Warm-rolling is carried out, control warm-rolling temperature adds up reduction ratio 63 ~ 79% at 123 ~ 237 DEG C；
7）Anneal under perhydro atmosphere protection, annealing temperature control at 550 ~ 597 DEG C, and at this temperature heat preservation 30 ~
40min；
8）It is cooled down, is cooled to room temperature in the case where cooling velocity is not less than 82 DEG C/s.
9. a kind of method for the precipitation enhancement type ferritic steel that yield strength is 900MPa grades is produced as claimed in claim 8,
It is characterized in that：The warm-rolling temperature adds up reduction ratio 66 ~ 73% at 136 ~ 227 DEG C.
10. a kind of method for the precipitation enhancement type ferritic steel that yield strength is 900MPa grades is produced as claimed in claim 8,
It is characterized in that：The annealing temperature is at 560 ~ 589 DEG C, and soaking time is in 32 ~ 37min.
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