CN110184532A - A kind of wear-resisting steel plate and its production method with excellent -60 DEG C of ultralow temperature impact flexibility - Google Patents
A kind of wear-resisting steel plate and its production method with excellent -60 DEG C of ultralow temperature impact flexibility Download PDFInfo
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- CN110184532A CN110184532A CN201810839036.7A CN201810839036A CN110184532A CN 110184532 A CN110184532 A CN 110184532A CN 201810839036 A CN201810839036 A CN 201810839036A CN 110184532 A CN110184532 A CN 110184532A
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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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- 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
- C21D8/0242—Flattening; Dressing; Flexing
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- 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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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- 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
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- 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
- C21D2211/008—Martensite
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Abstract
The present invention relates to a kind of quenching type low alloy wear resistance steel plate and its production method with excellent -60 DEG C of ultralow temperature impact flexibility, its chemical component wt% by weight contains: C:0.12~0.20%, Si:0.10~0.40%, Mn:0.8~1.30%, Nb:0.010~0.040%, V:0.020~0.050%, Ti :≤0.010%, Al:0.04~0.08%, Ni :≤0.1%, Cu :≤0.1%, Cr:0.20~0.60%, Mo:0.30~0.80%, B:0.001~0.005%, Ca :≤0.0015%, P :≤0.010%, S :≤0.0015%, O :≤0.0015%, N :≤0.0035%, H :≤0.0002%, and meet 0.16≤(Mn+Mo)/10+Cr/20≤0.26, S+P+O+N+H≤0.015%, surplus is Fe and inevitable impurity element.Processing step is: smelting -> external refining -> vacuum outgas -> continuous casting -> slab slow cooling processing -> heating -> rolling -> quenching -> destressing is rescued.Present component economy, simple process, steel plate are tiny lath martensite tissue, and comprehensive mechanical property is excellent, meets domestic and international big machinery industry to the requirement of low-temperature abrasion-resistant steel plate.
Description
Technical field
The invention belongs to field of steel metallurgy, and in particular to a kind of low conjunction with excellent -60 DEG C of ultralow temperature impact flexibility
Golden wear-resisting steel plate and its manufacturing method.
Background technique
The industry requirements such as wear-resisting steel plate is widely used in engineering machinery, mine is felled and transported, road transport intensity is high, wearability is good
Mechanical equipment critical component on, such as excavator-type shovel clamshell excavator, the middle pan of scraper conveyor, quarry tipper wagon box.Due to setting
In standby use process, there are complex working conditions such as various frictions, collision, impacts, abrasion-resistant stee other than requiring good wear-resisting property,
The toughness for also needing to have excellent.For example, quarry tipper wagon box, it is desirable in the falling from high altitude of mine large size building stones
It is indeformable under impact, it does not crack.
In recent years, domestic abrasion-resistant stee manufacturing enterprise has carried out a large amount of work to how to improve low-temperature impact toughness.China
Patent CN103103448A describes a kind of tough wear-resisting steel plate of 450HB rank low-alloy high-strength.The steel grade is using at offline modulation
Reason obtains lath martensite and granular bainite, guarantees -20 DEG C of low-temperature impact works of steel plate in 50J or more.Chinese patent
CN103146997B describes one kind and controls the side that cold mode produces the high-flexibility wear-resistant steel of hardness 400HB or more stage by stage online
Method.Steel plate is cooled to 400 DEG C after rolling, with the cooling velocity acceleration of 20 DEG C/s or more, is then air-cooled to room temperature, thin to obtain
Small martensite and the matching of a small amount of retained austenite (score≤5%) Lai Jinhang obdurability, -40 DEG C of low-temperature impact works can reach
60J.Chinese patent CN103205627B equally uses control by stages is cooling to obtain tiny martensite and a small amount of retained austenite
Obtain -40 DEG C of low-temperature impact toughness for being not less than 50J.The method that these three methods are all made of complex phase improves toughness, but due to going out
Granular bainite and the soft phase of retained austenite are showed, steel plate wearability will necessarily be affected to some extent.Chinese patent
CN104789881A produces one using no Mo, Ni or few Mo, Ni component system, using the method for laboratory quenching add-back fire
- 40 DEG C of low-temperature impact toughness >=40J high-strength tenacity wearing plates of kind.Low-temperature flexibility of steel plate under the conditions of steel mill's mass production is such as
What, needs to be further confirmed that.Above-mentioned patent is all made of tempering process and carries out obdurability matching adjusting and destressing processing, cost phase
To higher；Tempering temperature is low (400 DEG C of <) simultaneously, and tissue production is difficult.Currently, there is not yet having -60 DEG C of ultralow temperature impacts tough
Property quenching type wear-resisting steel plate production and research and development report.
With the enlargement of equipment, the further complication of applying working condition, such as Russian Siberia, Mongolia etc.
Extremely cold area, wearable device manufacturer gradually propose demand to -60 DEG C of ultralow temperature impact flexibility of wear-resisting steel plate.
Summary of the invention
It is a kind of with excellent -60 DEG C of ultralow temperature the technical problem to be solved by the present invention is to be provided for the above-mentioned prior art
The quenching type low alloy wear resistance steel plate and its manufacturing method of impact flexibility.The low alloy wear resistance steel plate microscopic structure is tiny horse
Family name's body；Tensile strength >=1300MPa, elongation percentage >=12%, -60 DEG C of Charpy V-type impact of collision function >=30J；Surface and center portion cloth
Family name's hardness is all satisfied 370~450HB.
The present invention solves the above problems used technical solution are as follows: one kind has excellent -60 DEG C of ultralow temperature impact flexibility
Quenching type low alloy wear resistance steel plate, the chemical component of the steel plate is calculated as C:0.12~0.20%, Si by mass percentage:
0.10~0.40%, Mn:0.8~1.30%, Nb:0.010~0.040%, V:0.020~0.050%, Ti :≤0.010%,
Al:0.04~0.08%, Ni :≤0.1%, Cu :≤0.1%, Cr:0.20~0.60%, Mo:0.30~0.80%, B:0.001
~0.005%, Ca :≤0.0010%, P :≤0.010%, S :≤0.0015%, O :≤0.0015%, N :≤0.0035%, H:
≤ 0.0002%, and meet 0.15≤(Mn+Mo)/10+Cr/20≤0.26, S+P+O+N+H≤0.015%, surplus is for Fe and not
Evitable impurity element.
Quenching type wear-resisting steel plate of the present invention with a thickness of 4~30mm.
The restriction reason of composition of steel is described below in the present invention:
C: the height of carbon largely determines the hardness level, toughness and welding performance of steel plate.Carbon content is low, hardness
Low, good toughness, excellent weldability；Carbon content is high, and completely, intensity is high for quenched martensite transformation, and hardness is high, and wearability is good, but steel
Plate plasticity and toughness reduce, and weldability is poor.It is needed based on steel plate hardness, wearability and weldability, carbon content control is in the present invention
0.12~0.20%.
Si: silicon, which is solid-solubilized in ferrite and austenite, improves intensity and hardness.Too high levels can deteriorate the tough of martensite steel
Property, while surface quality declines, and controls between 0.10~0.40%.
Mn: the strong harden ability for improving steel reduces martensite transfor mation critical cooling rate.It is above-mentioned when the content of manganese is lower
Effect is not significant, and armor plate strength and toughness are relatively low etc..Have the tendency that making grain coarsening when excessively high, while continuous casting slab segregation can be caused
Forming MnS, poor toughness and solderability reduces, therefore in view of the comprehensive of alloy is added, it is specified that manganese content additional amount is situated between in the present invention
In the range of 0.80~1.30%.
Nb: it is the formation element of strong C, N compound, plays the pinning effect to austenite grain boundary, inhibit when heated
Austenite grain is grown up.Significantly improve the intensity and toughness of steel simultaneously by crystal grain refinement.Additive amount is less than 0.010% timeliness
Fruit is unobvious, and toughness reduces when being greater than 0.040%, and continuous casting billet is caused to generate face crack.Therefore, present invention provide that content of niobium is answered
In the range of 0.010~0.040%.
V:VN, V (C, N) on the one hand hinder growing up for austenite grain during heating, play the role of refining crystal grain；
On the other hand the precipitate of these nanoscale small and disperseds distribution can significantly improve the intensity, hardness and wearability of steel plate.
Present invention provide that content of vanadium should be in the range of 0.020~0.050%.
Ti:Ti is carbide, and TiC particle is tiny, is distributed in crystal boundary, achievees the effect that refine crystal grain, together
Shi Tigao steel plate wearability.Ti and N also have extremely strong affinity simultaneously, it is easy to form the liquation TiN of micron order size, analyse
Object is hard out has wedge angle more, is unlikely to deform, unfavorable to the low temperature impact properties of steel plate；The present invention is to obtain excellent ultralow temperature punching
Performance is hit, does not allow that Ti element is added, clearly control Ti content≤0.010%.
Al: strong deoxidant element, while having stronger affinity with N, aging sensitivity caused by N element can be eliminated.Nization
The effect of fining austenite grains is played the role of in the precipitation of object, protects the harden ability of B element.In the present invention, do not allow to add
Ti element needs a certain amount of Al to consolidate N and protect B, it is specified that Al content must not be lower than 0.04%.Simultaneously because Al content is excessively high,
It will lead to the formation of excessive Al2O3 field trash, so that steel plate inspection does not conform to impact toughness decreased, therefore present invention provide that Al contains
Amount is not higher than 0.08%.
Ni, Cu: the most frequently used element of the low-temperature flexibility of steel is effectively improved.But since price is higher, economy is poor, this hair
The bright addition for cancelling Ni, Cu, substantially increases the cost competitiveness of invention steel grade.
Cr: reducing martensite transfor mation critical cooling rate, improves harden ability.Cr can also form (Fe, Cr) in steel3C、
(Fe, Cr)7C and (Fe, Cr)23The carbide such as C improve the intensity, hardness and wearability of steel.Cr is excessively high to reduce the solderable of steel plate
Connecing property.Therefore chromium content control is 0.20~0.80% in the present invention.
Mo: carbide, by influencing the diffusion rate of C, refinement carbide precipitate size refines crystal grain,
Significantly improve armor plate strength, hardness, wearability and toughness.Mo can greatly improve the element of steel hardenability simultaneously, be conducive to quench
The formation of full martensite when fiery improves steel plate impact flexibility.The control of Mo content is 0.30~0.80% in the present invention.
B: 0.001~0.005% micro B is added in the present invention, and main purpose is to improve the harden ability of steel plate, to subtract
The additive amount of other few precious metals, reduces cost.B more than 0.005% is easy to generate segregation, forms boride, seriously
Deteriorate steel plate toughness and reduces harden ability.
Commonly used to carry out inclusions class, changing the strips field trashes such as MnS is CaS equal sphere for Ca:Ca processing
Field trash reduces steel plate anisotropy, improves steel plate comprehensive performance.But in the present invention, the spherical impurities of the Ca such as CaS, CaO
Presence for pursue -60 DEG C of ultralow temperature impact flexibility it is equally unfavorable, therefore the present invention do not allow carry out Ca processing, control Ca contain
Amount≤0.0010%.
P: harmful element adversely affects material plasticity and toughness.The present invention pursues ultra-clean steel, and strict control P contains
Amount≤0.01%.
S: harmful element in steel adversely affects material plasticity and toughness.S content is high, easily the strips folder such as formation MnS
Sundries leads to steel plate anisotropy, is easy to happen delamination splitting.Due to not allowing to carry out Ca processing in the present invention, S is contained
Amount must carry out strict control, it is desirable that S :≤0.0015%.
O, N, H: pernicious gas element, content is high, and field trash is more, is also easy to produce white point, substantially reduces steel plate plasticity, toughness,
Generate cutting delayed crack.Strict control O content of the present invention is not higher than 0.0015%；N content is not higher than 0.0035%；H content
≤ 0.0002%.
In order to guarantee surface of steel plate hardness and centre hardness while meet the requirements, tiny lath martensite is obtained, substantially
Improve the wearability and -60 DEG C of ultralow temperature impact flexibility, strong harden ability element M n, the Cr of steel grade and refined carbides elements Mo of steel plate
Also need to meet 0.15≤(Mn+Mo)/10+Cr/20≤0.26.Meanwhile the sum of five-harmful elements S+P+O+N+H≤0.015%, significantly
The cold short tendency of steel plate is reduced, steel plate service life and crack resistance are improved.
The present invention separately provides a kind of preparation of above-mentioned low alloy wear resistance steel plate with excellent -60 DEG C of ultralow temperature impact flexibility
Method, concrete technology is as follows,
Smelting process: being smelted using converter mode, is then fed into LF refining furnace and is refined, and by VD or RH vacuum
Reason.Since molten steel does not allow to carry out Ca processing, the amount of inclusions must be in preceding working procedure strict control.BOF termination carbon content >=
0.06%, it is ensured that molten steel must not peroxidating, the formation for causing a large amount of oxides to be mingled with.LF depth desulfurization process, target call S≤
0.0010%；RH degassing, vacuum degree≤0.5mbar, time are not less than 30min.To prevent gas content from increasing after RH, as early as possible on
Continuous casting；Control the sum of S+P+O+N+H≤0.015%；Total rank≤2.5 of Control and Inclusion Removal A, B, C, D class.
Continuous casting process: in order to control steel plate internal defect, be segregated, progress Prepared by Low Superheat Pouring, whole argon for protecting pouring,
And dynamic soft-reduction control.Cast temperature is controlled in liquidus temperature TLAbove 5~20 DEG C, wherein
TL=1536-78C-7.6Si-4.9Mn-34P-30S-3.6Al-5Cu-1.3Cr-3.1Ni-2.0Mo -2.0V-
18Ti℃；
Slighter compress range restraint is in 0.4≤fs≤0.95, and wherein fs is solid phase number in slab, to guarantee that slab center is inclined
Analysis is not higher than C1.0 grades.
Slab retarded cooling process: after slab is offline, it is necessary to handled into hole or covering slow cooling.It handles start temperature and requires control
At 650-700 DEG C, the time must not be lower than 48 hours system.
Heating rolling technique: for the ultralow temperature impact flexibility for improving final steel plate, steel rolling process is mainly in following four side
It makes design in face: (1) using lower heating temperature, maximum temperature must not exceed 1200 DEG C.Slab is entered into stepped heating
Furnace is heated to 1150-1200 DEG C.Start to keep the temperature when center portion temperature reaches surface temperature, soaking time is not less than 30 minutes.Knot
Fruit shows that the technique can obtain relatively thin original austenite grains, improves steel plate low-temperature impact toughness.(2) using thick
Roll+finish rolling two-stage control rolling.The start rolling temperature of roughing is between 1050-1100 DEG C.Finish rolling start rolling temperature is between 840~900
℃.Lower finish rolling start rolling temperature can make austenite grain extend, and provide for subsequent ferrite forming core and further refinement
Basis.(3) biggish reduction ratio is used.Three percentage pass reduction >=15% after roughing.To temperature thickness >=3.0H, wherein H be at
Product thickness.Finish rolling total reduction >=66%.(4) due to quenching original template is bad when, and inhomogeneous cooling is even everywhere for steel plate, and it is poor to organize
It is different larger, plate property uniformity can be largely effected on, the reduction of ultralow temperature impact flexibility is caused.To guarantee the good template of steel plate,
Guarantee that quenching uniformity, the invention regulation hot rolled steel plate must not carry out pouring water control cold treatment.The control of hot rolled steel plate template unevenness
≤10mm/m。
Quenching heat treatment technique: steel plate is quenched after rolling, and 880~920 DEG C of hardening heat, furnace temperature to Wen Houbao
The warm time is 20~60min.For the uniformity for guaranteeing steel plate, temperature control precision is ± 10 DEG C.
Destressing processing: lonneal is generally taken to carry out destressing processing after the quenching of dilute-alloy martensite abrasion-resistant stee.By
Martensite can occur at >=80 DEG C in quenched martensite to decompose, lead to the precipitation of carbide, so that it is tough to influence steel plate impact
Property.Abrasion-resistant stee of the present invention cancels tempering process, using the cold strong progress destressing processing of strength, has been greatly reduced the life of abrasion-resistant stee
Produce cost.Strongly it is cold rectify after require steel plate unevenness≤5mm/m.
Compared with the prior art, the advantages of the present invention are as follows:
1) cancel adding for the noble metal Ni for being conducive to improve low-temperature impact toughness, Cu and rare earth element in Design of Chemical Composition
Enter, greatly reduces the cost of alloy of steel plate；
2) cancelling micro- Ti processing in Design of Chemical Composition (Ti :≤0.010%), reduces the inclusion particle of Ti to impact
And the influence of buckling performance, while greatly reducing cost of alloy；
3) cancel Ca processing (Ca≤0.0010%) in Design of Chemical Composition, reduce Ca processing each type impurity of bring
Influence of the particle to ultralow temperature impact flexibility, while greatly reducing alloy and process cost；
4) proportion of harden ability and carbide, 0.15≤(Mn+Mo)/10+ are controlled in Design of Chemical Composition
Cr/20≤0.26, it is ensured that surface of steel plate hardness and centre hardness are met the requirements simultaneously；Steel plate can get tiny full horse after quenching
Family name's body lath and tiny carbide, significantly improve steel plate low-temperature impact toughness and wearability；
5) strict control five-harmful elements and the field trash total amount upper limit in Design of Chemical Composition, the sum of S+P+O+N+H≤
0.015%, total rank≤2.5 of Control and Inclusion Removal A, B, C, D class substantially reduce the cold short tendency of steel plate, improve the punching of steel plate ultralow temperature
Hit toughness；
6) BOF smelt in strict control blow blocking content, 0.06% must not be lower than, substantially reduce and subsequent produced due to deoxidation
Raw each type oxide is mingled with, and leads to the reduction of ultralow temperature impact flexibility；
7) low overheat (≤20 DEG C) that uses of the present invention and dynamic soft-reduction technique, be effectively reduced steel plate center porosity and
Segregation (center segregation is not higher than C1.0 grades), steel plate thickness direction ingredient is uniform, and performance is stablized；
8) present invention uses lower slab reheating temperature≤1200 DEG C, lower finish rolling start rolling temperature and biggish finish rolling
Reduction ratio >=66%；Sufficiently refinement original austenite grains size, it is ensured that tiny martensitic structure, crystal grain ruler are obtained after quenching
Very little≤25um, to improve the final ultralow temperature impact flexibility of steel plate；
9) present invention cancels cooling control after rolling process, avoids accelerating cooling bring template problem, by controlling hot rolled steel plate
Unevenness≤10mm/m guarantees that quenching front spring is smooth, to reach the uniformity of steel plate quenching tissue and stress, greatly improves
Whole plate impact flexibility；Process cost is greatly reduced simultaneously, improves rhythm of production；
10) present invention cancels tempering process, using destressing processing is strongly rescued, avoids carbide in drawing process
Aggregation, which is precipitated, leads to the reduction of ultralow temperature impact flexibility, while reducing production cost, accelerates rhythm of production.Steel plate template is good
It is good, unevenness≤5mm/m；
11) steel plate high comprehensive performance of the present invention compares existing steel grade, and -60 DEG C of ultralow temperature impact flexibility are excellent >=30J；
The requirement of surface hardness and centre hardness can be met simultaneously.
12) the method for the present invention can be promoted and applied to other steel plates, such as high-strength marine worker deck of boat steel, Steels for High Rise Buildings,
Bridge steel plate, steel for engineering machinery, steels for pressure vessel use etc..
Detailed description of the invention
Fig. 1 is the test steel typical organization SEM electron-microscope scanning picture (2000X) of the embodiment of the present invention 1.
Specific embodiment
The present invention will be described in further detail below with reference to the embodiments of the drawings.
The technological process of production of unimach of the invention are as follows: pneumatic steelmaking -> LF refining -> VD or RH high vacuum is de-
Destressing is rescued in gas -> continuous casting -> slab slow cooling processing -> heating -> rolling -> quenches ->.
The production method with ultralow temperature impact flexibility wear-resisting steel plate of 1-2 of the embodiment of the present invention, includes the following steps:
(1) it smelts: using 150 tons of converter smeltings, BOF blows blocking 0.06%, is then fed into LF furnace and carries out refining deep desulfurization；
Upper continuous casting is handled by RH high vacuum degassing.Composition Control is shown in Table 1.
The chemical component (wt%) of 1 embodiment wear-resisting steel plate of table
(2) molten steel of smelting continuous casting: is cast into the continuous casting billet of 150mm thickness.Cast temperature is controlled in the above 5- of liquidus curve
25℃.Implement dynamic soft-reduction in casting process.Casting parameters are shown in Table 2.
(3) slab slow cooling is handled: continuous casting steel billet enters hole and carries out slow cooling, enters to cheat temperature and time and is shown in Table 2.
The control of 2 continuous casting process of table
(4) it rolls: continuous casting billet obtained by step (3) being put into walking beam furnace, is heated to 1200 DEG C, center portion to Wen Houkai
Begin to keep the temperature, soaking time 50 minutes.Steel billet carries out roughing+finish rolling two-stage control after high-pressure water descaling is handled after coming out of the stove and rolls
System.The start rolling temperature of roughing is between 1050-1100 DEG C, using heavy reduction rolling, three percentage pass reduction >=15% after roughing.
To temperature thickness >=3.0H.Finish rolling start rolling temperature is between 840-900 DEG C.Control hot rolled steel plate unevenness≤10mm/m.Related process
Parameter is shown in Table 3.
The control of 3 rolling mill practice of table
(5) quench: steel plate quenching temperature is 900 ± 10 DEG C, and soaking time is 30~60min, and hardening media is water.
(6) destressing is cold rectifys: quenched nickelclad enters the cold strong machine of strength and carries out destressing aligning.Control it is cold rectify after unevenness≤
5mm/m
(8) cold to rectify rear steel plate progress surface hardness, centre hardness, cross directional stretch, impact of collision test.
Specific ingredient, technological parameter are shown in Table 1~table 3.The corresponding performance of each example template is shown in Table 4.
The stretching of 4 embodiment of the present invention of table, impact and unevenness
Fig. 1 gives the microstructure photo that embodiment 1,2 tests steel.The microstructure of finished steel plate is uniform tiny
Lath martensite tissue, crystal grain is tiny, size≤25um.As it can be seen that passing through controlled rolling process control and suitable quenching process parameters
Selection, so that original austenite grains sufficiently refine, transgranular martensite lath is tiny, has fully ensured that -60 DEG C of steel plate are ultralow
Warm impact flexibility.
The present invention uses high-cleanness, high steel-making continuous casting technique, controlled rolling, out-line quenching and the cold strong technique of destressing, chemically
Ingredient design, base material tissue, field trash, center segregation, tempering temperature of quenching and time are angularly controlled, and guarantee surface of steel plate
While hardness, centre hardness, the elongation percentage of steel, -60 DEG C of ultralow temperature impact flexibility are good, while steel plate template is good, cutting
Indeformable afterwards, for engineering equipment, further enlargement, lightweight and low temperature use provide feasibility, have produce in batches and
The advantage and prospect of application.
In addition to the implementation, all to use equivalent transformation or equivalent replacement the invention also includes there is an other embodiments
The technical solution that mode is formed should all be fallen within the scope of the hereto appended claims.
Claims (10)
1. a kind of quenching type low alloy wear resistance steel plate with excellent -60 DEG C of ultralow temperature impact flexibility, it is characterised in that: its by with
The group of lower weight percent content is grouped as: C:0.12~0.20%, Si:0.10~0.40%, Mn:0.8~1.30%, Nb:
0.010~0.040%, V:0.020~0.050%, Ti :≤0.010%, Al:0.04~0.08%, Ni :≤0.1%, Cu :≤
0.1%, Cr:0.20~0.60%, Mo:0.30~0.80%, B:0.001~0.005%, Ca :≤0.0010%, P :≤
0.010%, S :≤0.0015%, O :≤0.0015%, N :≤0.0035%, H :≤0.0002%, and meet 0.15≤(Mn+
Mo)/10+Cr/20≤0.26, S+P+O+N+H≤0.015%, surplus are Fe and inevitable impurity element.
2. a kind of quenching type low-alloy wear-resistant steel with excellent -60 DEG C of ultralow temperature impact flexibility according to claim 1
Plate, it is characterised in that: the steel plate with a thickness of 4~30mm.
3. a kind of quenching type low-alloy wear-resistant steel with excellent -60 DEG C of ultralow temperature impact flexibility according to claim 1
Plate, it is characterised in that: the microscopic structure of the steel plate is tiny lath martensite, crystallite dimension≤25um.
4. a kind of quenching type low-alloy wear-resistant steel with excellent -60 DEG C of ultralow temperature impact flexibility according to claim 1
Plate, it is characterised in that: tensile strength >=1300MPa, elongation percentage >=12%, -60 DEG C of Charpy V-type impact of collision function >=30J；Surface
And center portion Brinell hardness is all satisfied 370~450HB；Template is good, steel plate unevenness≤5mm/m.
5. a kind of as described in claim 1 with the quenching type low alloy wear resistance steel plate of excellent -60 DEG C of ultralow temperature impact flexibility
Production method, which comprises the steps of:
(1) it smelts
It is smelted according to chemical component using converter mode, smelts and terminate carbon >=0.06%, and use external refining, high vacuum is de-
Gas；
(2) continuous casting
The degree of superheat of casting control is in liquidus temperature TLAbove 5~20 DEG C, slighter compress section meets 0.40≤fs≤0.95, wherein
Fs is solid phase number in slab, to guarantee center segregation of casting blank not higher than C1.0 grades；
(3) slab slow cooling is handled
Offline slab handle into hole or covering slow cooling, 600~700 DEG C of initial temperature, time >=48 hour；
(4) heating rolling
By continuous casting billet milling to target thickness；
(5) it quenches
Steel plate is quenched after rolling, 880~930 DEG C of hardening heat, furnace temperature to temperature after soaking time be 20~60min,
For the uniformity for guaranteeing steel plate, temperature control precision is ± 10 DEG C.
(6) destressing is aligned
Using the cold strong destressing of strength after steel plate quenching, steel plate unevenness≤5mm/m is controlled, which further removes steel plate and quench
Fiery stress, it is ensured that steel plate deformed and stress delayed crack will not be generated after user's cutting.
6. a kind of quenching type low-alloy wear-resistant steel with excellent -60 DEG C of ultralow temperature impact flexibility according to claim 5
The production method of plate, it is characterised in that: use Stand Mill two stages cooling controlling and rolling controlling process by continuous casting billet milling to target thickness, head
Slab is first heated to 1050-1200 DEG C, starts to keep the temperature when center portion temperature reaches surface temperature, soaking time is not less than 30 points
Clock, steel billet carry out roughing+finish rolling two-stage control rolling after high-pressure water descaling is handled after coming out of the stove.
7. a kind of quenching type low-alloy wear-resistant steel with excellent -60 DEG C of ultralow temperature impact flexibility according to claim 6
The production method of plate, it is characterised in that: the start rolling temperature of roughing after 1050-1100 DEG C, roughing three percentage pass reductions >=
15%, to temperature thickness >=3.0H, wherein H is finished product thickness, finish rolling start rolling temperature between 840~900 DEG C, crystalline substance roll reduction ratio >=
66%, During Controlled Rolling strict control unevenness≤10mm/m.
8. a kind of quenching type low-alloy wear-resistant steel with excellent -60 DEG C of ultralow temperature impact flexibility according to claim 5
The production method of plate, it is characterised in that: when smelting, is smelted using converter mode, be then fed into LF refining furnace and refined, and
By VD or RH application of vacuum, LF depth desulfurization process, target call S≤0.0010%；RH degassing, vacuum degree≤0.5mbar, when
Between be not less than 30min；To prevent gas content from increasing after RH, continuous casting is gone up as early as possible；Control the sum of S+P+O+N+H≤0.015%；Folder
Sundries controls total rank≤2.5 of A, B, C, D class.
9. a kind of quenching type low-alloy wear-resistant steel with excellent -60 DEG C of ultralow temperature impact flexibility according to claim 5
The production method of plate, it is characterised in that: the liquidus temperature in continuous casting process are as follows: TL==1536-78C-7.6Si-4.9Mn-
34P-30S-3.6Al-5Cu-1.3Cr-3.1Ni-2.0Mo-2.0V-18Ti℃。
10. a kind of quenching type low-alloy wear-resistant steel with excellent -60 DEG C of ultralow temperature impact flexibility according to claim 5
The production method of plate, it is characterised in that: for the ultralow temperature impact flexibility for improving final steel plate, when heating rolling mainly includes following
Content: 1) entering walking beam furnace for slab, is heated to 1150-1200 DEG C, starts when center portion temperature reaches surface temperature
Heat preservation, soaking time are not less than 30 minutes；2) using roughing+finish rolling two-stage control rolling, the start rolling temperature of roughing between
1050-1100 DEG C, finish rolling start rolling temperature is between 840~900 DEG C；3) biggish reduction ratio is used, three passages are depressed after roughing
Rate >=15%, to temperature thickness >=3.0H, wherein H is finished product thickness, finish rolling total reduction >=66%；4) hot rolled steel plate must not carry out
Pour water control cold treatment, hot rolled steel plate template unevenness control≤10mm/m.
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