CN107267859B - A kind of strong armour plate of superelevation and preparation method thereof - Google Patents
A kind of strong armour plate of superelevation and preparation method thereof Download PDFInfo
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- CN107267859B CN107267859B CN201710597134.XA CN201710597134A CN107267859B CN 107267859 B CN107267859 B CN 107267859B CN 201710597134 A CN201710597134 A CN 201710597134A CN 107267859 B CN107267859 B CN 107267859B
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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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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Abstract
The invention discloses strong armour plates of a kind of superelevation and preparation method thereof, belong to Plate Production technical field.The chemical component of the steel plate is by weight percentage are as follows: C:0.26~0.34%；Si:0.20-0.60%；Mn:1.1~1.4%；Nb:0.025~0.04%；Mo:0.5~1.0%；V:0.05~0.10%；Ti:0.01~0.04%；Al:0.01~0.06%；Ni:0~1.1%；Cu:0~0.6%；W:0.8~1.2%；P :≤0.010%；S :≤0.004%；N :≤0.008%；Remaining is Fe and inevitable impurity.The strong armour plate of superelevation of the present invention and preparation method thereof intensity rank covers 1800MPa-2000MPa, and material has good solderability, low-temperature impact toughness, cold formability energy and excellent ballistic performance.
Description
Technical field
The present invention relates to Plate Production technical field, in particular to a kind of strong armour plate of superelevation and preparation method thereof.
Background technique
Armour plate is typically employed in the projects such as shellproof protection is explosion-proof, and than range equipment, ballistic gate, bulletproof halmet is prevented
Play clothing, missile-resistant shield；Bank counter, confidential safety cabinet；Antiriot vehicle, ballproof cash truck, range equipment, armored personnel carrier, battlebus,
Submarine, landing craft, revenue cutter, helicopter etc., still, the cold formability of armour plate in the prior art can be poor, and bending is easily opened
It splits, can only be welded using the outer protective plate of method manufacture bullet-proof vehicle or the shellproof device of other complicated shapes of plurality of steel plates welding
Stitching heat-affected zone softened nearby causes the position ballistic performance to decline, especially the incomplete annealed zone in welding heat affected zone
It is punched during carrying out target practice test, causes security risk.
Summary of the invention
The present invention provides a kind of strong armour plate of superelevation and preparation method thereof, solves or part solves in the prior art
Armour plate cold formability can it is poor, bending is easy to crack, can only using plurality of steel plates welding method manufacture bullet-proof vehicle outside
The technical issues of protective plate or other complicated shapes shellproof device.
In order to solve the above technical problems, the present invention provides a kind of strong armour plate of superelevation, the chemical component of the steel plate
By weight percentage are as follows: C:0.26~0.34%；Si:0.20-0.60%；Mn:1.1~1.4%；Nb:0.025~0.04%；
Mo:0.5~1.0%；V:0.05~0.10%；Ti:0.01~0.04%；Al:0.01~0.06%；Ni:0~1.1%；Cu:0
~0.6%；W:0.8~1.2%；P :≤0.010%；S :≤0.004%；N :≤0.008%；Remaining is Fe and inevitable miscellaneous
Matter.
Further, the steel plate with a thickness of 2-12mm.
Another aspect of the invention provides a kind of preparation method of strong armour plate of superelevation, comprising the following steps: by iron
Continuous casting obtains slab after the molten steel that water passes through ingredient described in converter or electric furnace smelting, LF refining or RH refining acquisition claim 1；
After the slab is carried out heating furnace reheating, hot rolled plate is obtained using roughing, finish rolling；It is cold that the hot rolled plate is subjected to laminar flow
But after, coil of strip is obtained using curling is coiled；The coil of strip is subjected to slow cooling, obtains finished product using continuous heat；Wherein,
The slab is heated to 1240~1280 DEG C in heating furnace, and heating time is greater than 210 minutes, carry out roughing, finish rolling it is described
The workpiece thickness of slab uses 5 times~10 times finished product thicknesses, and entry temperature at finishing is 1000 DEG C~1080 DEG C, and finishing temperature is
830~880 DEG C, the coil of strip carries out slow cooling and carries out section cooling using leading portion refrigerating mode, and target coiling temperature is 650 DEG C~
750℃。
Further, slow cooling processing is carried out using burial pit after the coil of strip is offline, slow cooling time is greater than 72 hours, coil of strip
Go out to cheat at extremely≤150 DEG C of slow cooling.
Further, it includes: the coil of strip after slow cooling to be carried out uncoiling, then carry out that the coil of strip, which carries out continuous heat,
Aligning；The coil of strip after aligning is subjected to high-frequency induction heating, is then quenched, then carry out induction tempering heating；It will sense
Coil of strip progress after should being tempered is crosscutting, obtains the finished product.
Further, the coil of strip carries out continuous high frequency induction heating, and heating temperature is 850-950 DEG C, and the rate of heat addition is big
In 100 DEG C per second.
Further, the coil of strip after high-frequency induction heating is kept the temperature, soaking time was less than 10 minutes.
Further, coil of strip after heating is quenched, using water quenching, target temperature is room temperature.
Further, high-frequency induction tempering heating is carried out to coil of strip after quenching, heating temperature is 250~450 DEG C, heating speed
Rate is greater than 100 DEG C per second.
Further, to tempering heating after coil of strip keep the temperature, soaking time less than 20 minutes, after be air-cooled to room temperature.
The present invention provides a kind of shield steel plates and preparation method thereof, and C chemical component by weight hundred is added in steel plate
Divide than being 0.26~0.34%, Mn chemical component is 1.1~1.4% by weight percentage, and Si chemical component is by weight percentage
For 0.20-0.60%, carbon equivalent is controlled by control C, Si additional amount, Mn content proof strength is properly increased, is adopted in terms of alloy
Strengthened with the compound addition of Ni, Cu, in addition adding Nb improves original steel plate structural state, and it is endless to add a certain amount of V improvement welding
Full weight crystal region intensity, W chemical component are 0.8~1.2% by weight percentage, and purpose is to improve welding heat affected zone bullet-proof
The ballistic performance of energy and steel plate after the raising of continuous bullet strike temperature, guarantees the harden ability of material by adding high Mo, sufficiently
Play build up, the strengthening effects such as precipitation strength, then by roughing, finish rolling, continuous heat process modification, produce excess of export
High-strength armour, material have good solderability, ballistic performance, cold formability energy and low-temperature impact toughness, obtained superelevation
Strong armour plate, tensile strength are greater than 1800MPa, and elongation percentage is greater than 8%, and -20 DEG C of ballistic works are greater than 40J, 180 ° of clod wash B=
35mm/D=6a does not crack, and material has good welding performance and ballistic performance simultaneously.
Detailed description of the invention
Fig. 1 is the metallographic structure figure of the strong armour plate of superelevation provided in an embodiment of the present invention；
Fig. 2 is the precipitate electromicroscopic photograph of the strong armour of superelevation in Fig. 1.
Specific embodiment
Referring to Fig. 1-2, a kind of shield steel plate provided in an embodiment of the present invention, the chemical component of the steel plate by weight hundred
Divide ratio are as follows: C:0.26~0.34%；Si:0.20-0.60%；Mn:1.1~1.4%；Nb:0.025~0.04%；Mo:0.5~
1.0%；V:0.05~0.10%；Ti:0.01~0.04%；Al:0.01~0.06%；Ni:0~1.1%；Cu:0~0.6%；
W:0.8~1.2%；P :≤0.010%；S :≤0.004%；N :≤0.008%；Remaining is Fe and inevitable impurity.It is described
Steel plate with a thickness of 2-12mm.
Carbon: carbon plays a significant role in heat treatment high-strength steel, is on the one hand remarkably improved the strong of material by adding C
Degree improves bulletproof ability, but low-temperature impact toughness and solderability to guarantee material, needs to do bound clearly limiting, this
The carbon content that uses is invented as 0.25~0.34%.
Silicon: silicon is solution strengthening element, but the excessively high silicon of addition can have a negative impact to the plasticity of material.Present invention addition
Silicone content is 0.20-0.60%%.
Manganese: manganese has solution strengthening effect, while material harden ability can be improved, be improve strength of materials important element it
One, but excessively high be easy to produce of manganese content addition is segregated and can reduce toughness of material, deteriorates performance.Add since the present invention controls C
Enter amount, Mn additional amount can be properly increased, it is 1.1~1.4% that the present invention, which adds manganese content,.
Sulphur and phosphorus: sulphur and P elements are excessively high to adversely affect to toughness of material and plasticity.Present invention defines sulfur contents
It should control within 0.004%, phosphorus content should control within 0.01%.
Aluminium: aluminium is deoxidant element, while having certain grain refining effect.It is 0.01% present invention defines aluminium content
~0.06%.
Molybdenum: material harden ability can be improved in molybdenum, and control heat treatment cools tissue refines crystal grain, improves material plasticity and intensity.
The present invention is added to the Mo of 0.50%-1.00%, improves the contribution of build up, substitutes addition B using high Mo, improves material
Whole plasticity and toughness.
Niobium: the main purpose for adding Nb is refinement crystal grain, and cooperation can be obtained tiny using lower finish rolling area rolling temperature
Uniform ferrite crystal grain, heat treatment base-material fine microstructures to subsequent heat treatment have genetic effect, be conducive to improve finally at
The obdurability of product steel plate；On the other hand, Nb has precipitation strength effect simultaneously, is conducive to the intensity and the hot shadow of weld seam that improve material
Ring the performance in area.The Nb content that the present invention adds is 0.025%~0.04%.
Titanium: the main function of titanium is fixed nitrogen in the present invention, reduces the N to dissociate in steel by forming TiN, improves materials'use
Performance；In addition, extra Ti in conjunction with C, plays the role of precipitation strength, but the precipitation strength of TiC can be to the low-temperature impact of material
Toughness causes damages, therefore needs upper control limit.The present invention adds 0.01-0.04%Ti.
Vanadium: the present invention is designed to the addition that the important alloying element for setting up meter separately is high V, and the coiling temperature of hot rolling considers V
The precipitation strength and tissue thinning effect of element.The V of present invention addition 0.05%~0.10% carries out microalloying, and cooperation is suitable
Production technology, the precipitate of the V of a large amount of small and disperseds distribution has been obtained in hot-rolled coil, during tempering heat treatment into
The precipitate that V is precipitated in one step greatly improves the strength level of material, while the precipitate of weld seam hot showing area V can organize austenite long
Greatly, heat affected zone organization is refined, weld heat-affected zone comprehensive performance is improved.
Cu: the purpose that Cu is added in the present invention is to improve the integral strength of material；The present invention adds 0.3~0.6%Cu；
Ni: the purpose that Ni is added in the present invention is to improve the toughness of material, avoids cracked after addition Cu, while high Ni
The ballistic performance for being conducive to improve material is added and improves property of welded joint, the present invention adds 0.6~1.1%Ni.
Nitrogen: the plasticity and toughness of the excessively high meeting severe exacerbation material of nitrogen content, especially for heat treatment high-strength steel, therefore,
The present invention, which limits nitrogen content, should be less than 0.008%.
W: chemical component core design of the present invention is addition W element, and W, which is added, can be improved the intensity of armour, heat resistance
And temper resistance, the crystal grain of steel is grown up when reducing quenching, improves property of welded joint.Meanwhile addition W can be improved steel plate and exist
Continuous shooting of practicing shooting, the ballistic performance after temperature raising.The present invention adds 0.8-1.2W%.
The controlling of production process main points that the present invention uses are smelting process strict control P, S, N content guarantee slab matter
Amount.Each controlled rolling and cooling process parameter of operation of rolling strict control, coil of strip batch laggard burial pit and carry out slow cooling processing, and heat can be improved
Roll the performance uniformity and strip shape quality of roll bending.
It is 0.26~0.34%, Mn chemistry that technical scheme adds C chemical component in steel plate by weight percentage
Ingredient is that 1.1~1.4%, Si chemical component is 0.20-0.60% by weight percentage by weight percentage, by controlling C, Si
Additional amount controls carbon equivalent, properly increases Mn content proof strength, is strengthened in terms of alloy using the compound addition of Ni, Cu, in addition added
Nb is added to improve original steel plate structural state, adding a certain amount of V improves the incomplete annealed zone intensity of welding, and W chemical component is pressed
Weight percent is 0.8~1.2%, and purpose is to improve welding heat affected zone ballistic performance and steel plate in continuous bullet strike temperature
Ballistic performance after raising guarantees the harden ability of material by adding high Mo, sufficiently sends out to avoid the occurrence of massive martensite lath
Wave the strengthening effects such as build up, precipitation strength, then by roughing, finish rolling, continuous heat process modification, produce superelevation
Strong armour, material have good solderability, ballistic performance, cold formability energy and low-temperature impact toughness, and obtained superelevation is strong
Armour plate, tensile strength are greater than 1800MPa, and elongation percentage is greater than 8%, and -20 DEG C of ballistic works are greater than 40J, 180 ° of clod wash B=
35mm/D=6a does not crack, and material has good welding performance and ballistic performance simultaneously.
The ingredient mentality of designing of low C, middle Mn, high Mo, high V high W in the application use, give full play to build up, are precipitated
The strengthening effects such as strengthen, produce the strong armour of superelevation, material have good solderability, ballistic performance, cold formability energy and
Low-temperature impact toughness.
The strong armour plate chemical component of superelevation described herein use in low C, low Si, high Mn design, by control C,
Si additional amount controls carbon equivalent, properly increases Mn content proof strength, is strengthened in terms of alloy using the compound addition of Ni, Cu, in addition
Adding Nb improves original steel plate structural state, add a certain amount of V and improve and weld incomplete annealed zone intensity, the most core
It is designed as addition W element, purpose is to improve welding heat affected zone ballistic performance and steel plate after the raising of continuous bullet strike temperature
Ballistic performance.Guarantee that the harden ability of material does not add Cr and B to avoid the occurrence of massive martensite lath by adding high Mo
Element.
The controlling of production process main points that the application uses are smelting process strict control P, S, N content guarantee slab matter
Amount.
Another aspect of the invention provides a kind of preparation method for producing the strong armour plate of above-mentioned superelevation, including following
Step:
Step 1, molten iron is obtained into ingredient described in claim 1 by converter or electric furnace smelting, LF refining or RH refining
Continuous casting obtains slab after molten steel.
Step 2, after the slab being carried out heating furnace reheating, hot rolled plate is obtained using roughing, finish rolling.
Step 3, after the hot rolled plate being carried out section cooling, coil of strip is obtained using curling is coiled.
Step 4, the coil of strip is subjected to slow cooling, obtains finished product using continuous heat.
Wherein, specific process parameter control is as follows:
The slab is heated to 1240~1280 DEG C in heating furnace, and heating time is greater than 210 minutes, soaking time according to
1~1.5min/mm of effective thickness is calculated, and is to guarantee austenite homogenization and alloy member using the purpose of higher heating temperature
The compound of element such as Ti, Nb, V for being formed in slab dissolve more abundant.
The workpiece thickness for carrying out the slab of roughing, finish rolling uses 5 times~10 times finished product thicknesses, guarantees to have enough
Austenite Unhydrated cement drafts, be conducive to refine crystal grain；Intermediate base length can be shortened simultaneously by increasing workpiece thickness,
It is poor into finish rolling head and tail temperature to reduce, prevent tail temperature from reducing excessive increase mill load.Entry temperature at finishing is 1000
DEG C~1080 DEG C, it is obtain fine uniform crystal grain effective using lower finish rolling area temperature that finishing temperature, which is 830~880 DEG C,
Method avoids the appearance of hot-rolled coil organizational coarseness and banded structure.
The coil of strip carries out slow cooling and carries out section cooling using leading portion refrigerating mode, and target coiling temperature is 650 DEG C~750
℃.On the one hand be conducive to reinforce the build up after phase transformation, be on the other hand conducive to enhance precipitating reinforcing effect, obtain more iron
Tiny precipitation product in ferritic, to effectively improve the strength of materials.The target coiling temperature that the present invention uses for 650 DEG C~
750 DEG C, the alternate precipitation and the precipitation in ferrite for being mainly in view of V, Nb, Ti, coiling temperature lower limit need strict control big
In 650 DEG C, avoids occurring bainite structure in hot-rolled coil, influence strip shape quality.
The coil of strip it is offline after using burial pit carry out slow cooling processing, slow cooling time be greater than 72 hours, coil of strip slow cooling to≤
Go out to cheat at 150 DEG C.Slow cooling is carried out to coil of strip using burial pit, the logical volume mechanical property of material can be made more uniform, and can be with
Effectively internal stress is made to be released and homogenize, so as to improve strip shape quality, is conducive to subsequent heat treatment plate shape and residual stress
Control.
Step 4 is discussed in detail.
The coil of strip carries out continuous heat
Step 41, the coil of strip after slow cooling is subjected to uncoiling, then is aligned.
Step 42, the coil of strip after aligning is subjected to high-frequency induction heating, is then quenched, then carry out induction tempering
Heating.
Step 43, the coil of strip progress after induction tempering is crosscutting, obtain the finished product.
Wherein, it is as follows to carry out the control of continuous heat specific process parameter for the coil of strip:
The coil of strip carries out continuous high frequency induction heating, and heating temperature is 850-950 DEG C, and the rate of heat addition is greater than per second 100
℃.It is to control quenched martensite tissue topography using the purpose of high-frequency induction heating, improves the rate of heat addition and be conducive to quench
To more tiny martensite and lath of bainite, and be conducive to control morphology of carbides in quenching structure.
Coil of strip after high-frequency induction heating is kept the temperature, soaking time was less than 10 minutes.Soaking time is controlled, can be reduced
Austenite Grain Growth, and prevent the carbide dissolution of V, Ti, Nb in hot-rolled coil；Steel plate after heating and thermal insulation is quenched
Processing, using water quenching, target temperature is room temperature, and tiny martensite+bainite structure can be obtained after quenching.
Coil of strip after heating is quenched, using water quenching, target temperature is room temperature.High frequency is carried out to coil of strip after quenching
Induction tempering heating, heating temperature are 250~450 DEG C, and the rate of heat addition is greater than 100 DEG C per second.Coil of strip after tempering heating is carried out
Heat preservation, soaking time less than 20 minutes, after be air-cooled to room temperature.It is to control the carburizing bodily form using the purpose that induction is quickly heated
Looks；Steel plate after tempering heating is kept the temperature, soaking time was less than 20 minutes, when being kept the temperature by quickly heating with strict control
Between, the tiny cementite being discontinuously distributed can be obtained, the precipitation of Ti is retained, and the intensity of material is improved.Using in 250-450 DEG C
High tempering, at the same be conducive to eliminate steel plate residual stress, be conducive to control material unevenness and guarantee blanking after it is indeformable.
Each controlled rolling and cooling process parameter of operation of rolling strict control, coil of strip batch laggard burial pit and carry out slow cooling processing, can
Improve the performance uniformity and strip shape quality of hot-rolled coil.
In order to become apparent from the embodiment of the present invention, introduced from the application method of the embodiment of the present invention below.
The weight percent of the chemical component of the strong armour element of superelevation is shown in Table 1:
The strong armour plate specific embodiment chemical component of 1 superelevation of table
The preparation method is as follows:
S2: being put into heating furnace for slab and heat, and controls heating temperature and soaking time.
S3: being put into milling train for the slab after heating and roll, and controls finish rolling inlet and outlet temperatures, obtains target thickness
Steel plate.
S4: cooling down hot rolled plate, carries out section cooling using leading portion refrigerating mode, hot rolled plate after cooling is carried out
It batches, obtains steel plate finished product；Target oiler temperature control in coiling process is 650-750 DEG C；The thick 2-12mm of steel plate finished product.
S5: carrying out slow cooling processing using burial pit after offline to hot-rolled sheet coil, and slow cooling time is greater than 72 hours, coil of strip slow cooling
Go out to cheat at extremely≤150 DEG C.
S6: continuous high frequency induction heating and heat preservation, rear water quenching to room temperature are carried out to coil of strip.
S7: carrying out induction tempering heating and heat preservation to steel plate after quenching, after be air-cooled to room temperature.
The specific processing parameter of 1-7 embodiment is shown in Table 2:
The strong armour plate embodiment processing parameter of 2 superelevation of table
The mechanical property of the strong armour plate of superelevation is shown in Table 3 after the heat treatment of 1-7 embodiment:
The specific shooting scheme of table 4 and result
It is strong to give full play to solid solution by the ratio of chemical component in rational design steel for the strong armour of superelevation provided by the invention
The strengthening effects such as change, phase transformation strengthening, build up, precipitation strength make the steel plate finished product finally obtained have good intensity, tough
Property, welding performance and strip shape quality.Material simultaneously, has the protective performance of superelevation with excellent comprehensive mechanical property, fits
For 1-2 grades of 4569 ballistic standard of NATO protection and the protection of other Europe superscripts, American Standard and national standard armour appropriate level.
It should be noted last that the above specific embodiment is only used to illustrate the technical scheme of the present invention and not to limit it,
Although being described the invention in detail referring to example, those skilled in the art should understand that, it can be to the present invention
Technical solution be modified or replaced equivalently, without departing from the spirit and scope of the technical solution of the present invention, should all cover
In the scope of the claims of the present invention.
Claims (8)
1. a kind of preparation method of the strong armour plate of superelevation, the chemical component of the strong armour plate of superelevation is by weight percentage
Are as follows: C:0.26~0.34%；Si:0.20-0.60%；Mn:1.1~1.4%；Nb:0.025~0.04%；Mo:0.5~
1.0%；V:0.05~0.10%；Ti:0.01~0.04%；Al:0.01~0.06%；Ni:0~1.1%；Cu:0~0.6%；
W:0.8~1.2%；P :≤0.010%；S :≤0.004%；N :≤0.008%；Remaining is Fe and inevitable impurity, spy
Sign is that the preparation method comprises the following steps:
Continuous casting obtains slab after molten iron is obtained molten steel by converter or electric furnace smelting, LF refining or RH refining；
After the slab is carried out heating furnace reheating, hot rolled plate is obtained using roughing, finish rolling；
After the hot rolled plate is carried out section cooling, coil of strip is obtained using curling is coiled；
The coil of strip is subjected to slow cooling, obtains finished product using continuous heat；
It includes: the coil of strip after slow cooling to be carried out uncoiling, then aligned that the coil of strip, which carries out continuous heat,；After aligning
The coil of strip carry out high-frequency induction heating, then quenched, then carry out induction tempering heating；Described in after induction tempering
Coil of strip progress is crosscutting, obtains the finished product；
Wherein, the slab is heated to 1240~1280 DEG C in heating furnace, and heating time is greater than 210 minutes, carries out roughing, essence
The workpiece thickness of the slab rolled uses 5 times~10 times finished product thicknesses, and entry temperature at finishing is 1000 DEG C~1080 DEG C, eventually
Rolling temperature is 830~880 DEG C, and the coil of strip carries out slow cooling and carries out section cooling, target coiling temperature using leading portion refrigerating mode
It is 650 DEG C~750 DEG C.
2. preparation method according to claim 1, it is characterised in that:
The steel plate with a thickness of 2-12mm.
3. preparation method according to claim 1, it is characterised in that:
Slow cooling processing is carried out using burial pit after the coil of strip is offline, slow cooling time is greater than 72 hours, and coil of strip slow cooling is to≤150 DEG C
When go out cheat.
4. preparation method according to claim 1, it is characterised in that:
The coil of strip carries out continuous high frequency induction heating, and heating temperature is 850-950 DEG C, and the rate of heat addition is greater than 100 DEG C per second.
5. preparation method as claimed in claim 4, it is characterised in that:
Coil of strip after high-frequency induction heating is kept the temperature, soaking time was less than 10 minutes.
6. preparation method as described in claim 1, it is characterised in that:
Coil of strip after heating is quenched, using water quenching, target temperature is room temperature.
7. preparation method as described in claim 1, it is characterised in that:
High-frequency induction tempering heating is carried out to coil of strip after quenching, heating temperature is 250~450 DEG C, and the rate of heat addition is greater than per second 100
℃。
8. preparation method as claimed in claim 7, it is characterised in that:
To tempering heating after coil of strip keep the temperature, soaking time less than 20 minutes, after be air-cooled to room temperature.
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| CN109930075B (en) * | 2019-04-12 | 2020-08-14 | 贝斯山钢(山东)钢板有限公司 | Bulletproof steel plate for armor and manufacturing method thereof |
| CN113528974B (en) * | 2021-06-18 | 2022-06-21 | 首钢集团有限公司 | Steel for protection and preparation method thereof |
| CN113549842A (en) * | 2021-06-21 | 2021-10-26 | 首钢集团有限公司 | High-strength bulletproof helmet shell and preparation method thereof |
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| CN1308144A (en) * | 2000-12-25 | 2001-08-15 | 钢铁研究总院 | High-performance impact resisting steel |
| CN103205634A (en) * | 2013-03-28 | 2013-07-17 | 宝山钢铁股份有限公司 | Low-alloy high-hardness wear-resistant steel plate and manufacturing method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1308144A (en) * | 2000-12-25 | 2001-08-15 | 钢铁研究总院 | High-performance impact resisting steel |
| CN103205634A (en) * | 2013-03-28 | 2013-07-17 | 宝山钢铁股份有限公司 | Low-alloy high-hardness wear-resistant steel plate and manufacturing method thereof |
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