CN104975234B - A kind of 550MPa grades of non-aqueous cold and hot Mechanical course technique steel and its production method - Google Patents
A kind of 550MPa grades of non-aqueous cold and hot Mechanical course technique steel and its production method Download PDFInfo
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- 239000012535 impurity Substances 0.000 claims abstract description 6
- 238000005096 rolling process Methods 0.000 claims description 65
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- 238000010583 slow cooling Methods 0.000 claims description 11
- 239000000470 constituent Substances 0.000 claims description 3
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- 238000001556 precipitation Methods 0.000 description 13
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- 238000005728 strengthening Methods 0.000 description 5
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-UHFFFAOYSA-N 0.000 description 5
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Abstract
A kind of 550MPa grades of non-aqueous cold and hot Mechanical course technique steel and its production method that the present invention is provided, wherein, the technique steel at least includes：The impurity F e of 0 0.08% C, 0 0.010% P, 0 0.005% S, 1.0% 1.5% Mn, 0.70% 1.0% Si, 0.2% 0.4% Ni, 1.0% 1.5% Cr, 0.5% 0.8% Mo, 1.2% 1.6% Cu, 0.06% 0.20% V, 0.01% 0.04% Re and surplus.The present invention realizes the yield strength >=550MPa of formed technique steel, tensile strength >=620MPa, ballistic work >=100J at 60 DEG C.
Description
Technical field
The invention belongs to thermomechanical control technology field, more particularly to a kind of 550MPa grades of non-aqueous cold and hot Mechanical course
Technique steel and its production method.
Background technology
TMCP(Thermo Mechanical Control Process：Thermomechanical control technique) be in the hot rolling,
On the basis of the controlled rolling (Control Rolling) of control heating-up temperature, rolling temperature and drafts, then control cooling
And accelerate the technology general name of cooling (Accelerated Cooling).TMCP technologies are mainly by fining austenite grains, control
Various methods such as system rolling and control cooling are combined to realize, without excessive alloying element, it is not required that follow-up complicated
The steel of high-intensity high-tenacity can be produced under heat treatment condition, is the production work of a kind of low cost, low energy consumption, high benefit
Skill.
However, traditional TMCP technologies, are all that water spray rapid cooling or water spray are ultrafast cold after controlled rolling, water is accelerated after controlled rolling
It is cold easily cause surface of steel plate and internal cooling speed difference and make surface and it is internal produce residual stress, make the unevenness of steel plate and
Bendability degenerates；Particularly when cooling velocity is very big, massive energy welding point heat affected area HAZ can be caused significantly soft
Change, cause the intensity and toughness of steel relatively low.
The content of the invention
The present invention provides a kind of 550MPa grades of non-aqueous cold and hot Mechanical course technique steel and its production method, solves or part
Water-cooled is accelerated to easily cause surface of steel plate and internal cooling speed difference and make surface and inside after solving controlled rolling in the prior art
Produce residual stress, the technological deficiency for causing the intensity and toughness of steel relatively low.
According to one aspect of the present invention, there is provided a kind of 550MPa grades of non-aqueous cold and hot Mechanical course technique steel, the steel
At least include：Mn, 0.70%-1.0%'s of S, 1.0%-1.5% of P, 0-0.005% of C, 0-0.010% of 0-0.08%
Cu, 0.06%- of Mo, 1.2%-1.6% of Cr, 0.5%-0.8% of Ni, 1.0%-1.5% of Si, 0.2%-0.4%
The Re of 0.20% V, 0.01%-0.04% and impurity F e of surplus；Wherein, the yield strength of the steel is more than or equal to
550MPa, tensile strength is more than or equal to 620MPa, and ballistic work at -60 DEG C is more than or equal to 100J.
Optionally, in the steel, the constituent content of the Ni, the Cr, the Mo and the Cu meets following formula：
(Ni+Cr+Mo)/Cu≥1.0。
According to another aspect of the present invention, there is provided a kind of 550MPa grades of non-aqueous cold and hot Mechanical course technique steel producer
Method, including：By heating strand and it is incubated so that the abundant austenitizing of the strand after heating；To the institute of abundant austenitizing
State strand roughing；To treating warm treatment by the strand after roughing；Finish rolling will be carried out after the strand after temperature treatment, obtained
Steel plate；To the steel plate stacking slow cooling that obtains to room temperature.
Optionally, it is described by heating strand and to be incubated so that the abundant austenitizing of the strand after heating includes：By institute
State heating strand to 1050~1100 DEG C；The strand after to heating is incubated 4~6h so that the strand after heating is abundant
Austenitizing.
Optionally, the strand roughing to abundant austenitizing includes：To the strand at 1020 ± 20 DEG C
Start roughing；The drafts that 2 passages are ensured in rough rolling process is 15~20%；The accumulative drafts of rough rolling step is 50~70%,
Rolling speed is 1.5-2m/min.
Optionally, described pair in the strand after roughing treats warm processing procedure, roughing finishing temperature is 950 ± 20
℃。
Optionally, it is described to carry out finish rolling and include after the strand after temperature treatment：The finish rolling in α+γ two-phase sections, and essence
Preceding 2 passage deformation quantity control is rolled 20~25%, and extreme trace time deformation quantity is gradually decreased, and finish rolling end temp is controlled in 660-700
℃；Wherein, the α+γ two-phase sections are 660-820 DEG C.
The present invention provide a kind of 550MPa grades of non-aqueous cold and hot Mechanical course technique steel, by will at least following Elements Cs, P,
S, Mn, Si, Ni, Cr, Mo, Cu, V, Re and impurity F e, synthesize the technique steel, by the Mn to institute according to rational ratio
The austenite for stating steel is adjusted to the temperature of ferritic transformation, and then adjusts the hot processing temperature interval of the steel, and it is right to realize
The tensile strength of the steel is adjusted；And combined and separated out with the carbon atom in the steel by the Cr so as to described
Steel produces precipitation strength；And the incubation period that the steel medium pearlite changes is extended by the Mo, realize making iron element in the steel
Body and perlitic range are moved to right；And cause to separate out ε-Cu in the steel by the Cu, and then produce precipitation strength；And by institute
State the carbon in V and the steel, nitrogen and combine to form second phase particles, produce precipitation strength；And by the P, the S, the Ni
With the Re, at least the one kind in following performances of the steel is adjusted：Segregation performance, welding performance, low-temperature impact are tough
Property and ductile-brittle transition temperature；And be adjusted by the accounting to the Si in the steel so that often added in the steel
1% Si, the yield strength of the steel at least increases 100MPa.So that the yield strength of the technique steel for being formed >=
550MPa, tensile strength >=620MPa, ballistic work >=100J at -60 DEG C.
Brief description of the drawings
In order to illustrate more clearly about the embodiment of the present invention or technical scheme of the prior art, below will be to institute in embodiment
The accompanying drawing for needing to use is briefly described, it should be apparent that, drawings in the following description are only some implementations of the invention
Example, for those of ordinary skill in the art, on the premise of not paying creative work, can also obtain according to these accompanying drawings
Obtain other accompanying drawings.
Fig. 1 is 550MPa grades provided in an embodiment of the present invention non-aqueous cold and hot Mechanical course technique steel production method flow chart；
Fig. 2 is the steel plate schematic illustration of tissue in example provided in an embodiment of the present invention 1；
Fig. 3 is the steel plate schematic illustration of tissue in example provided in an embodiment of the present invention 2；
Fig. 4 is the steel plate schematic illustration of tissue in example provided in an embodiment of the present invention 3；And
Fig. 5 is the steel plate schematic illustration of tissue in example provided in an embodiment of the present invention 4.
Specific embodiment
Below in conjunction with the accompanying drawing in the embodiment of the present invention, the technical scheme in the embodiment of the present invention is carried out clear, complete
Site preparation is described, it is clear that described embodiment is only a part of embodiment of the invention, rather than whole embodiments.It is based on
Embodiment in the present invention, the every other embodiment that those of ordinary skill in the art are obtained belongs to present invention protection
Scope.
A kind of 550MPa grades of non-aqueous cold and hot Mechanical course technique steel provided in an embodiment of the present invention and its production method, realize
A kind of yield strength of offer is more than or equal to 550MPa (steel plate thickness can select 10-35mm), and the non-water-cooled TMCP techniques of use
The high-strength technique steel manufactured.The technique steel is strong using solution strengthening, dislocation strengthening and precipitation by rational composition design
The methods such as change are combined, and the non-water-cooled TMCP techniques such as suitable drafts and final rolling temperature control in α+γ two-phase sections, make
Obtain produced steel grade yield strength and be more than or equal to 550MPa, tensile strength is more than or equal to 620MPa, and ballistic work at -60 DEG C is big
In equal to 100J, while steel plate template is good, welding performance is excellent, low production cost, the characteristics of with wide adaptability.
Specifically, described 550MPa grades non-aqueous cold and hot Mechanical course technique steel at least includes following composition：0-0.08%
C, 0-0.010% P, 0-0.005% S, 1.0%-1.5% Mn, 0.70%-1.0% Si, 0.2%-0.4%
V, 0.01%- of Cu, 0.06%-0.20% of Mo, 1.2%-1.6% of Cr, 0.5%-0.8% of Ni, 1.0%-1.5%
The 0.04% Re and impurity F e of surplus.
Wherein, for the C in technique steel：The content of C is less than or equal in embodiments of the present invention in technique steel
0.08%, because C is one of element of indispensable raising steel strength in steel, in order to ensure high tenacity, excellent welding
Property and cold forming etc., C content is limited in≤0.08% between, while the intensity of steel is ensured, suitable life can be reached again
Produce the technique effect of operation.For P and S in technique steel：P easily causes segregation in technique steel, deteriorates welding, and pole
Easily the low-temperature impact toughness for reducing steel is adversely affected with ductile-brittle transition temperature etc. is improved.Meanwhile, S easily with technique steel in
Mn combine to form MnS and be mingled with, so as to influence the low-temperature impact toughness of technique steel.Therefore, in the embodiment of the present invention, should try one's best and subtract
Lack adverse effect of P, S element to Steel Properties, thus controlled in P≤0.010%, S ＜ 0.005%.
For the Ni in technique steel：Ni is a kind of solution strengthening element in technique steel, can improve ferrite base
The intensity of body.Meanwhile, Ni is remarkably improved the low-temperature flexibility of steel, reduces ductile-brittle transition temperature, can effectively prevent in technique steel because
Cu hot-short and the check crack that causes.For the Cr in technique steel：Cr strong carbides separate out element, energy and technique in technique steel
Carbon atom in steel combines a large amount of precipitations, so as to produce precipitation strength.Additionally, Cr can also improve technique steel atmospheric corrosion resistance and
The ability of seawater corrosion.For the Mo in technique steel：Mo can effectively extend the incubation period of perlitic transformation in technique steel, make
Ferrite and pearlite region moves to right, while the influence very little also to bainitic transformation.
In addition, for the Cu in technique steel：Cu is in technique steel as strong precipitation strength element so that separated out in steel
A large amount of tiny ε-Cu, produce strong precipitation strength, can make up the loss of strength caused by C content in steel.Additionally, Cu is also
The atmospheric corrosion resistance of steel can be improved, particularly effect becomes apparent when Cu, Cr are added simultaneously.For the V in technique steel
For：V can be combined with C, N in technique steel and be formed second phase particles, can also produce precipitation strength.So that without addition in steel
The alloying elements such as Nb, Ti, mainly due to NbC, the solution temperature of the particle such as TiC, NbN, TiN is higher, temperature during heating strand
Need to be below 1100 DEG C, so as to have a negative impact to plate surface quality.
For the Mn in technique steel：Mn is solution strengthening element in technique steel, addition 1.0-1.5%'s
Mn can reduce temperature of the austenite to ferritic transformation, expand hot processing temperature interval.Meanwhile, Mn easily convert the austenite to for
M-A tissues of hard, and occurring to be accompanied by Volume Changes when M-A changes, soft ferrite is produced plastic deformation,
Mobile dislocation is produced on M-A and ferrite interface.Even if this mobile dislocation is also susceptible to fortune under small stress
It is dynamic, so as to cause the reduction of steel grade yield strength, but the processing hardening that removable dislocation is produced, then steel grade tensile strength can be caused to carry
It is high.For the Si in technique steel：Si has certain solution strengthening element to the intensity of technique steel so that often added in steel
1% Si, its yield strength can increase 100MPa.For the Re in technique steel：Re is purified in technique steel as crystal boundary
Element, can play a part of to improve the low-temperature flexibility of steel.
From above-mentioned narration, the embodiment of the present invention exactly it is innovative will at least following Elements Cs, P, S, Mn, Si, Ni, Cr,
Mo, Cu, V, Re and impurity F e, the technique steel is synthesized according to rational ratio so that and the yield strength of the technique steel >=
550MPa, tensile strength >=620MPa, ballistic work >=100J at -60 DEG C, and steel plate template are good, and welding performance is excellent；
And production cost is relatively low, easily implement in industrial production.
It should be noted that in this technique steel, under the constituent content of the Ni, the Cr, the Mo and the Cu meets
State formula：(Ni+Cr+Mo)/Cu≥1.0.The precipitation of liquid Cu when so on the one hand can hinder heating strand, on the other hand
The second phase particles that the carbides such as Cr, Mo are separated out in rolling or phase transformation, ε-Cu size separations during as stacking slow cooling
The core for going out, so as to refine the ε-Cu purpose for reaching precipitation strength.
Fig. 1 is referred to, the embodiment of the present invention additionally provides a kind of 550MPa grades non-aqueous cold and hot Mechanical course technique steel production
Method, comprises the following steps：
Step 101, by heating strand and is incubated so that the abundant austenitizing of the strand after heating；
Specifically, can be by the heating strand to 1050~1100 DEG C, then to described in after heating in the step 101
Strand is incubated 4~6h so that the abundant austenitizing of the strand after heating.
Step 102, the strand roughing to abundant austenitizing, rolling speed is 1.5-2m/min；
Step 103, to treating warm treatment by the strand after roughing；
Step 104, will carry out finish rolling after the strand after temperature treatment, obtain steel plate；
Step 105, to the steel plate stacking slow cooling that obtains to room temperature.
Wherein, after the abundant austenitizing of strand after heating, the strand is started slightly at 1020 ± 20 DEG C
Roll, ensure that the drafts of 2 passages is 15~20% in rough rolling process, the accumulative drafts of rough rolling step is 50~70%, rolling speed
Rate is 1.0-2.5m/min, and in rough rolling step controlled rolling, treats to ensure roughing finishing temperature 950 ± 20 in warm processing procedure
℃.Then the finish rolling in α+γ (660-820 DEG C) two-phase section, the control of 2 passage deformation quantities is in 20~25%, extreme trace time shape before finish rolling
Variable is gradually decreased, and finish rolling end temp is controlled at 660-700 DEG C.After finish rolling, steel plate is without water-spraying control, stacking slow cooling to room
Temperature, forms the technique steel.
It is noted that burning steel technology, and rough rolling step high temperature big Reduction Technology at a slow speed using low temperature in steel making technology.
This is mainly when the Cu contents in steel are higher, easily forms one layer of liquation layer in casting billet surface.These liquations layer, it is difficult to pass through
, so as to cause plate surface quality to be deteriorated, there are the surfaces such as more iron scale press-in, pockmark and lack in high-pressure water descaling and removal
Fall into.Additionally, in rough rolling step big pressure deformation at a slow speed, strand center portion can be made fully to deform and recrystallize, so as to effectively refine brilliant
Grain, improves steel plate center portion performance.Meanwhile, the finish rolling stage rolls in α+γ two-phase sections, and particularly preceding 2 passage deformation quantity control exists
20-25% or so, on the one hand can produce a large amount of dislocations in ferrite and austenite, second when being conducive to air cooling and stacking slow cooling
Phase particle, the especially precipitation of ε-Cu.On the other hand, due to add Mo, V separate out second phase particles as ferrite or shellfish
The forming core core of family name's body, so that the crystallite dimension organized when refining air cooling.Stacking Slow cooling after rolling, mainly uses steel plate
Waste heat after rolling, on the one hand eliminates the internal stress that steel plate is produced by phase transformation and deformation, on the other hand can then ensure solid in steel
The precipitation of molten Cu and microalloy element, improves armor plate strength and plasticity.Further, since cooldown rate is slower, in cooling procedure
Being organized as obtaining is uniform, and influence of the non-equilibrium microstructure formed by rapid cooling to steel plate welding performance can be avoided during welding.
Below, by example 1-3 cold and hot Mechanical course technique steel non-aqueous to 550MPa grades provided in an embodiment of the present invention and
Its production method is described in further details, to support the technical problems to be solved by the invention.
Example 1
In example 1, the chemical analysis of technique steel can be as described below：0.08%C, 1.5%Mn, 1.0%Si, P≤
0.010%, S ＜ 0.005%, 0.4%Ni, 1.0%Cr, 0.5%Mo, 1.2%Cu, 0.06%V, 0.01%RE, balance of Fe.
Wherein, in process of production by thickness for the slab of 250mm is heated to 1050 DEG C in stove and is incubated 240min.Then 1020
DEG C start roughing, roughing speed 1.0m/min, in rough rolling process, the 2nd, the deformation quantity of 3 passages be 20%, then treat temperature, roughing
930 DEG C of finishing temperature.Whole process adds up drafts 70%.After roughing terminates, 780 DEG C of beginning finish rolling, 660 DEG C of finish rolling terminate,
Steel plate rolling thickness is 20mm, and 2 passage deformation quantity 25% before finish rolling, extreme trace time deformation quantity is gradually decreased.After finish rolling, stacking slow cooling
To room temperature.The steel plate tissue for ultimately forming is reference can be made to shown in Fig. 2, mechanical property can be as shown in table 1 below.
Example 2,
In example 2, the chemical analysis of technique steel can be as described below：0.08%C, 1.5%Mn, 1.0%Si, P≤
0.010%, S ＜ 0.005%, 0.4%Ni, 1.0%Cr, 0.5%Mo, 1.2%Cu, 0.06%V, 0.01%RE, balance of Fe.
Wherein, in process of production by thickness for the slab of 250mm is heated to 1100 DEG C in stove and is incubated 360min.Then 1040
DEG C start roughing, roughing speed 2.5m/min, the 3rd, the deformation quantity of 4 passages be 15%, then controlled rolling treats temperature to 970 DEG C
Finish to gauge.Rough rolling step adds up drafts 70%.After roughing terminates, 820 DEG C of beginning finish rolling, 700 DEG C of finish rolling terminate, and steel plate rolling is thick
It is 30mm to spend, 2 passage deformation quantity 20% before finish rolling, and extreme trace time deformation quantity is gradually decreased.After finish rolling, stacking slow cooling to room temperature.Most
End form into steel plate tissue can be found in shown in Fig. 3, mechanical property can be as shown in table 1 below.
Example 3
In example 3, the chemical analysis of technique steel can be as described below：0.045%C, 1.0%Mn, 0.7%Si, P≤
0.010%, S ＜ 0.005%, 0.2%Ni, 1.5%Cr, 0.8%Mo, 1.6%Cu, 0.20%V, 0.04%RE, balance of Fe.
Wherein, in process of production by thickness for the slab of 250mm is heated to 1080 DEG C in stove and is incubated 300min.Then 1030
DEG C start roughing, roughing speed 1.5m/min, the 2nd, the deformation quantity of 3 passages be 18%, after controlled rolling, 960 DEG C of finish to gauges, roughing
Stage adds up drafts 60%.After roughing terminates, 820 DEG C of beginning finish rolling, 680 DEG C of finish rolling terminate, and steel plate rolling thickness is 10mm,
2 passage deformation quantity 25% before finish rolling, extreme trace time deformation quantity is gradually decreased.After finish rolling, stacking slow cooling to room temperature.The steel for ultimately forming
Plate tissue can be found in shown in Fig. 4, and mechanical property can be as shown in table 1 below.
Example 4
In example 4, the chemical analysis of technique steel can be as described below：0.06%C, 1.2%Mn, 0.85%Si, P≤
0.010%, S ＜ 0.005%, 0.35%Ni, 1.2%Cr, 0.6%Mo, 1.4%Cu, 0.10%V, 0.02%RE, it is balance of
Fe.It is the heating strand of 250mm to after 1090 DEG C of isothermal 250min by thickness, 1000 DEG C of beginning roughing, roughing speed 2.0m/
Min, the deformation quantity 18% of the 2nd, 3 passages in rough rolling process, 950 DEG C of finish to gauge after controlled rolling, whole process adds up drafts
50%.After roughing terminates, 800 DEG C of beginning finish rolling, 670 DEG C of finish rolling terminate, and steel plate rolling thickness is 35mm, third and fourth road of finish rolling
Secondary deformation quantity 20%, extreme trace time deformation quantity is gradually decreased.After finish rolling, stacking slow cooling to room temperature.The steel plate tissue for ultimately forming can
Shown in Figure 5, mechanical property can be as shown in table 1 below.
Table 1
, but those skilled in the art once know basic creation although preferred embodiments of the present invention have been described
Property concept, then can make other change and modification to these embodiments.So, appended claims are intended to be construed to include excellent
Select embodiment and fall into having altered and changing for the scope of the invention.
Obviously, those skilled in the art can carry out various changes and modification without deviating from essence of the invention to the present invention
God and scope.So, if these modifications of the invention and modification belong to the scope of the claims in the present invention and its equivalent technologies
Within, then the present invention is also intended to comprising these changes and modification.
Claims (4)
1. a kind of 550MPa grades non-aqueous cold and hot Mechanical course technique steel production method, it is characterised in that including：
By heating strand and it is incubated so that the abundant austenitizing of the strand after heating；
The strand roughing to abundant austenitizing；
To treating warm treatment by the strand after roughing；
Finish rolling will be carried out after the strand after temperature treatment, obtain steel plate；
To the steel plate stacking slow cooling that obtains to room temperature；
Wherein, it is described by heating strand and to be incubated so that the abundant austenitizing of the strand after heating includes：
By the heating strand to 1050~1100 DEG C；
The strand after to heating is incubated 4~6h so that the abundant austenitizing of the strand after heating；
Wherein, the technique steel at least includes：S, 1.0%-1.5% of P, 0-0.005% of C, 0-0.010% of 0-0.08%
Mn, 0.70%-1.0% Si, 0.2%-0.4% Ni, 1.0%-1.5% Cr, 0.5%-0.8% Mo, 1.2%-
The Re of V, 0.01%-0.04% of 1.6% Cu, 0.06%-0.20% and impurity F e of surplus；Wherein, the technique steel
Yield strength is more than or equal to 550MPa, and tensile strength is more than or equal to 620MPa, and ballistic work at -60 DEG C is more than or equal to 100J；And
In the technique steel, the constituent content of the Ni, the Cr, the Mo and the Cu meets following formula：(Ni+Cr+Mo)/
Cu≥1.0。
2. 50MPa grades as claimed in claim 1 non-aqueous cold and hot Mechanical course technique steel production method, it is characterised in that described
The strand roughing to abundant austenitizing includes：
Roughing is started to the strand at 1020 ± 20 DEG C；
The drafts that 2 passages are ensured in rough rolling process is 15~20%；
The accumulative drafts of rough rolling step is 50~70%.
3. 50MPa grades as claimed in claim 2 non-aqueous cold and hot Mechanical course technique steel production method, it is characterised in that：
Described pair in the strand after roughing treats warm processing procedure, roughing finishing temperature is 950 ± 20 DEG C.
4. 50MPa grades as claimed in claim 3 non-aqueous cold and hot Mechanical course technique steel production method, it is characterised in that described
Include finish rolling is carried out after the strand after temperature treatment：
20~25%, extreme trace time deformation quantity gradually subtracts the control of 2 passage deformation quantities before finish rolling, and finish rolling in α+γ two-phase sections
Few, finish rolling end temp is controlled at 660-700 DEG C；Wherein, the α+γ two-phase sections are 660-820 DEG C.
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