CN104525912A - Lining plate and preparation method thereof - Google Patents
Lining plate and preparation method thereof Download PDFInfo
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- CN104525912A CN104525912A CN201410655634.0A CN201410655634A CN104525912A CN 104525912 A CN104525912 A CN 104525912A CN 201410655634 A CN201410655634 A CN 201410655634A CN 104525912 A CN104525912 A CN 104525912A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D19/00—Casting in, on, or around objects which form part of the product
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B7/00—Layered products characterised by the relation between layers; Layered products characterised by the relative orientation of features between layers, or by the relative values of a measurable parameter between layers, i.e. products comprising layers having different physical, chemical or physicochemical properties; Layered products characterised by the interconnection of layers
- B32B7/04—Interconnection of layers
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Abstract
The invention discloses a lining plate; a carbide coating layer is arranged on the upper surface of a working surface of the lining plate; a matrix of the lining plate is alloy steel; and the invention further provides a preparation method for obtaining the lining plate. The lining plate has the carbide coating layer on the working surface; the carbide coating layer comprises a V2C compact ceramic layer, and can further comprise a micron V8C7 compact ceramic layer and a fusion layer of V8C7 and the matrix. The V2C compact ceramic layer, the micron V8C7 compact ceramic layer and the fusion layer of V8C7 and the matrix are gradiently distributed in sequence. The lining plate can be applied to the surface of the alloy steel. A matrix and vanadium compound body obtained through casting is externally leaded in an external carbon source, and is heated and insulated to form the carbide coating layer on the surface of the matrix; and the coating layer and the matrix are metallurgically bonded, so that the binding force is strong, the problems of weak binding force and easy particle dropping due to traditional non-metallurgical bonding between hard particles and a metal matrix are overcome, and the wear resistance of the working surface of the lining plate is largely improved.
Description
Technical field
The present invention relates to a kind of composite liner with wear-resistant coating and preparation method thereof, particularly relate to and a kind of there is composite liner of wear resistant carbide coating and preparation method thereof, be specifically related to a kind of wear resistant carbide coating composite liner being applied to steel alloy surface and preparation method thereof.
Background technology
In the industrial trades such as metallurgy, mine, electric power, building materials, the fragmentation, grinding, conveying etc. of material, all will use a large amount of liner plates, and liner plate subjects washing away and wearing and tearing in various degree, and change frequent, expending greatly, is main consumable accessory.Current every profession and trade liner material quality used mainly contains several single metal material such as potassium steel, Low Alloying Multicomponent Steels, Cr series white cast iron.Potassium steel, only under high load capacity, high impact stresses, realizes austenite work hardening to martensitic solid-state phase changes, just can give full play to its wearability, and yield strength is low, easily produces plastic flow; The matrix hardness of Low Alloying Multicomponent Steels is at 500-1000HV
0.1in scope, change, low compared with the hardness of cementite and alloy carbide, can not resist press-in and the paddling of abrasive material, and in use surface produces a large amount of cuttings and flow low-cycle fatigue, therefore abrasive wear resistant weld deposit poor-performing; Although Cr series white cast iron is wear-resisting, heat-resisting, corrosion resisting property is good, its poor toughness easily ruptures, and use is restricted.For the concrete operating mode of wear liner, domestic and international many scholars develop various new high-abrasive material, mainly contain modified high manganese steel, medium managese steel, ultra-high manganese steel series, high, medium and low carbon wear-resisting alloy steel series, manganese system, boron system 2 wear-resistant white cast and the liner material quality such as martensite, bainite abrasion-resistant nodular cast iron, but because single material mechanical mechanics property in intensity, hardness, plasticity and toughness etc. can not be taken into account or there is particular/special requirement to military service operating mode, service life is still very short, is difficult to the requirement meeting various operating mode.
But the hardness only improving liner plate matrix material is still not enough to the persistence that ensures that it is on active service, therefore increasing coating in its working position is the economical and effective means of this problem of solution.It is the coating of carbide material that present stage uses more, and hardness is high, abrasion resistance properties is superior feature that it has, covers alloy base surperficial wearability and the life-span can improving the parts prepared by matrix material with coating way.Wherein VC
pbe a kind of common coating material, it has following advantageous features:
(1) physical and chemical performance of the excellences such as density is low, intensity is high, elastic modelling quantity is high, anti-oxidant, wear-resisting, corrosion-resistant is possessed;
(2) tendency of growing up in sintering process is little, and particle is generally rounded, is a kind of ideal reinforcing material;
(3) vanadium resource enriches, and easily obtain, less expensive, vanadium carbide obtains and generally applies in metal-base composites;
(4) have very high heat endurance and the face-centred cubic structure of high rigidity, closely, this is convenient to be combined with steel substrate better for lattice paprmeter and lattice types and austenite;
(5) VC
pstandard enthalpy of formation △ G
0be worth low, its synthetic reaction is easy to carry out;
(6) VC
pthe steel-based composite material of coating except hardness is high, wearability well except, machinable, forging, welding, heat treatment reinforcement and be out of shape little, and there is the cold and hot working performance of common steel-smelting.
Therefore, VC
pcoating material is widely used as the wearing face of chipless cold/hot metal machining tool, cutting tool, various mould, antiwear heat resisting is anti-corrosion part.
The method preparing carbide coating at present has chemical vapour deposition technique, physical vaporous deposition, heat spraying method, hot plating method etc., but these methods, there is the deficiencies such as production equipment requirement is harsh, production efficiency is low, anchoring strength of coating is low.
Therefore how VC is obtained at liner plate working surface
pcoating, and the preparation method selecting that a kind of production equipment is simple, technological process is short, obtain with good, the difficult drop-off of basal body binding force and the coating of mechanical property, anti-wear performance excellence is problem demanding prompt solution.
Summary of the invention
The defect existed for above-mentioned prior art and deficiency, the object of the present invention is to provide a kind of liner plate, and the surface of its working position has a kind of wear-resistant coating, and this wear-resistant coating is V
2c dense ceramic layers, its chemical stability and wearability good, there is low-friction coefficient, high rigidity, low-surface-energy and low thermal conductiv-ity; And further, provide a kind of preparation method for obtaining above-mentioned liner plate.
Further, the present invention also provides a kind of liner plate, the surface of its working position has a kind of gradient composite coating, it is preferably coated on liner plate matrix surface, to improve wearability and the fracture toughness on its surface, particularly potassium steel or low-alloy high-tensile structural steel surface, and a kind of preparation method for obtaining above-mentioned coating is provided.
Described liner plate, has wear-resistant coating at its plate body working surface.Due to plate body profile and size varied, the preparation method of backing surface wear-resistant coating involved in the present invention is applicable to all types of liner plate.Plate body working surface has very high hardness and good wearability, and plate body body portion has good toughness.
For realizing the object of the invention, present invention employs following technical scheme:
Surface has a liner plate for wear-resistant coating, and this wear-resistant coating is V
2c dense ceramic layers; Preferably, V
2c dense ceramic layers is as the criterion monocrystalline phase, and described accurate monocrystalline refers to mutually, between polycrystalline phase and monocrystalline mutually between, compared to polycrystalline phase, uniform orientation is high, crystal boundary obviously reduces, and the microscopic structure that atomic arrangement is more orderly.
More preferably, along V
2c dense ceramic layers longitudinal profile, its thickness is 7-25 μm, is preferably 12-22 μm, is more preferably 15-20 μm; Preferably, wherein V
2the volume fraction of C is greater than 80%, is preferably greater than 90%; Preferably, V
2c crystallite dimension is 20-50 μm, is preferably 30-50 μm.
In addition, the present invention also provides a kind of surface to have the liner plate of gradient composite coating, and described gradient composite coating is carbide coating, comprises the V of distribution gradient successively
2c dense ceramic layers, micron V
8c
7dense ceramic layers, V
8c
7with the fused layer of matrix.
Preferably, V
2c dense ceramic layers is as the criterion monocrystalline phase, and described accurate monocrystalline refers to mutually, between polycrystalline phase and monocrystalline mutually between, compared to polycrystalline phase, uniform orientation is high, crystal boundary obviously reduces, and the microscopic structure that atomic arrangement is more orderly.
More preferably, along V
2c dense ceramic layers longitudinal profile, its thickness is 7-25 μm, is preferably 12-22 μm, is more preferably 15-20 μm; Preferably, wherein V
2the volume fraction of C is greater than 80%, is preferably greater than 90%; Preferably, V
2c crystallite dimension is 20-50 μm, is preferably 30-50 μm.
Further preferably, along micron V
8c
7dense ceramic layers longitudinal profile, its thickness is 15-90 μm, is preferably 40-88 μm, is more preferably 70-88 μm; Preferably, V
8c
7volume fraction be greater than 70%, be preferably greater than 75%; Preferably, V
8c
7crystallite dimension be 5-15 μm, be preferably 6-15 μm, be more preferably 8-15 μm.
Still more preferably, along V
8c
7with the fused layer longitudinal profile of matrix, its thickness is 123 μm-1095 μm, is preferably 300-1069 μm; Preferably, wherein V
8c
7volume fraction be 20%-85%, be preferably 50%-85%; Preferably, V
8c
7crystallite dimension be 5-20 μm, be preferably 10-20 μm.
Preferably, gradient composite coating gross thickness is 145-1210 μm, preferably at 400-1180 μm.
More preferably, liner plate matrix is according to heat treatment mode one or more that can be divided in pearlite, martensite, ferrite, bainite, austenite and sorbite different; Preferably, this gradient composite coating is applied in steel alloy surface.
The invention provides the preparation method that a kind of surface has the liner plate of wear-resistant coating, comprise the steps:
1) first prepare a vanadium plate, preferably, wherein the Pureness control of vanadium is at 99.7-99.9%; More preferably, the THICKNESS CONTROL of described vanadium plate is at 0.2-3mm; Preferably, described vanadium plate is first by addition surface treatment;
2) according to liner plate size, sand mold is made; Preferably, CO is used
2waterglass hardened sand, precoated sand, self-hardening resin sand or tide mould sand make sand mold.According to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, and backing surface fixed outer carbon source bottom sand mold, is then placed in backing surface bottom sand mold by vanadium plate accordingly, and itself and external carbon source are combined closely;
3) steel alloy base material is smelted for molten steel;
4) poured into by above-mentioned molten steel in the above-mentioned sand mold being placed with vanadium plate and external carbon source, after molten steel cooled and solidified, take out foundry goods, sand removal process, obtaining bottom liner plate is alloy steel matrix, and liner plate upper surface is the complex with vanadium plate; Preferably, pouring temperature controls at 1500-1560 DEG C; More preferably, the duration of pouring, 10-50 was advisable second; Further preferably, after one minute, at hot topping; Preferably, room temperature cooling;
5) the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere, finally cools to room temperature with the furnace, thus forms wear-resistant coating at backing surface, and liner plate matrix is still alloy steel matrix.
Wherein, wear-resistant coating is V
2c dense ceramic layers.
Preferably, this V is obtained by control temperature retention time, holding temperature
2c dense ceramic layers; Preferably, V
2c dense ceramic layers is as the criterion monocrystalline phase, and described accurate monocrystalline refers to mutually, between polycrystalline phase and monocrystalline mutually between, compared to polycrystalline phase, uniform orientation is high, crystal boundary obviously reduces, and the microscopic structure that atomic arrangement is more orderly.
The present invention also provides a kind of surface to have the preparation method of the liner plate of gradient composite coating, comprises the steps:
1) first prepare a vanadium plate, preferably, wherein the Pureness control of vanadium is at 99.7-99.9%; More preferably, the THICKNESS CONTROL of described vanadium plate is at 0.2-3mm; Preferably, described vanadium plate is first by addition surface treatment;
2) according to liner plate size, sand mold is made; Preferably, CO is used
2waterglass hardened sand, precoated sand, self-hardening resin sand or tide mould sand make sand mold.According to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, and backing surface fixed outer carbon source bottom sand mold, is then placed in backing surface bottom sand mold by vanadium plate accordingly, and itself and external carbon source are combined closely;
3) steel alloy base material is smelted for molten steel;
4) poured into by above-mentioned molten steel in the above-mentioned sand mold being placed with vanadium plate and external carbon source, after molten steel cooled and solidified, take out foundry goods, sand removal process, obtaining bottom liner plate is alloy steel matrix, and liner plate upper surface is the complex with vanadium plate; Preferably, pouring temperature controls at 1500-1560 DEG C; More preferably, the duration of pouring, 10-50 was advisable second; Further preferably, after one minute, at hot topping; Preferably, room temperature cooling;
5) the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere, finally cools to room temperature with the furnace, thus forms wear-resistant coating at backing surface, and liner plate matrix is still alloy steel matrix.
6) surface of gained there is gradient composite coating liner plate by further heat treatment to obtain more suitably matrix.
Preferably, vanadium plate thickness is 0.2-3mm; If be less than 0.2mm, then vanadium plate just complete reaction in cast recombination process, can not obtain V
2c organizes, and directly generates Dispersed precipitate V
8c
7; Then cause diffusion length to increase more than 3mm, reaction power is not enough.
Preferably, by strict rate-determining steps 5) in holding temperature and the relation of time, obtain described accurate monocrystalline phase V
2c dense ceramic layers.This ceramic layer presents comparatively obvious accurate single crystal organization, and show as crystal boundary under light microscope and reduce, affect the dislocation also corresponding minimizing of fracture toughness, the sub boundary in generation increases, and effectively improves the anti-crack ability of this ceramic layer.
Preferably, by rate-determining steps 5) in temperature retention time, holding temperature obtain this gradient composite coating and carbide coating, described carbide coating comprises the accurate monocrystalline phase V of distribution gradient successively
2c dense ceramic layers, micron V
8c
7dense ceramic layers, V
8c
7with the fused layer of matrix.
More preferably, above-mentioned steps 5) in holding temperature, temperature retention time and the gross thickness of gradient composite coating that finally can obtain meet following formula,
L＝kTlogt
1/2+b
0
Wherein:
The gross thickness (μm) of L---gradient composite coating,
K---be constant, value is 0-1, k ≠ 0,
T---holding temperature (K),
T---temperature retention time (s),
B
0---original depth (μm), the thickness of the composite bed formed after namely molten steel is poured into a mould and between vanadium plate.
To sum up, described gradient composite coating, comprises V
2c dense ceramic layers, hardness is high.Described V
2c dense ceramic layers is as the criterion monocrystalline phase, and described accurate monocrystalline refers to mutually, the arrangement of atom unlike monocrystalline there is identical lattice like that, but still there is strict order, present geometry arrangement; Uniform orientation is high, crystal boundary obviously reduces, and atomic arrangement is more orderly.Accurate monocrystalline is between polycrystalline phase with monocrystalline phase, and compared to polycrystalline phase, the crystal boundary of accurate monocrystalline phase obviously reduces, and dislocation density is low, has more sub boundary, and therefore hardness has obvious lifting; And than monocrystalline phase, it requires lower to preparation method, and organize more stable.
Preferably, in step 1) in, surface-treated step is as follows:
First step pickling, selects the hydrogen peroxide of the hydrochloric acid of 300ml/L or the phosphoric acid of 60ml/L or 120ml/L, rear running water;
Second step pickling, selects the hydrogen peroxide of the hydrofluoric acid of 300ml/L or the sulfuric acid of 200ml/L or 240ml/L, rear running water;
3rd step surface finish, selects 800-1200 object Al
2o
3sand paper, finally uses alcohol ultrasonic cleaning.
More preferably, step 2) in external carbon source be graphite paper or graphite powder; Preferably, described graphite paper is more than three grades, and purity is 85-99%, and thickness is 0.1-0.35mm; Preferably, described graphite powder selects granularity at 600-1000 order, and purity is 85-99%.
Preferably, step 5) in, be warming up to 1000-1160 DEG C, programming rate controls at 7 DEG C/min, and temperature retention time is 6-12h, preferred 8-10h.
Preferably, selected alloy steel matrix is low-alloy high-tensile structural steel or potassium steel.
Preferably, protection gas is argon gas or nitrogen, and gas flow is 5-7ml/min.
Wherein, holding temperature should be strict controlled in above-mentioned scope, and temperature is higher than 1160 DEG C, and the liquid phase in course of reaction is too much, and makes V
2c is transformed into V
8c
7, and accurate monocrystalline phase V can not be obtained
2c; But temperature is lower than 1000 DEG C, then the solubility of V is too low, and reaction cannot be carried out by forward.Same, temperature retention time also should keep one reasonably interval, the time more than 12h, nearly all V
2c can change V into
8c
7, and lower than 6h, then react the V of acquisition
2very little, coating layer thickness is difficult to ensure C, and best should remain on 8-10h.
More preferably, the liner plate complex with carbide coating is by further heat treatment to obtain more suitably matrix, and heat treatment step is:
A () is when matrix is potassium steel, its heat treatment step is: after water-tenacity treatment, obtain single austenite structure, preferably, concrete heat treatment step is: within 1 hour, be warmed up to 300-400 DEG C, then 1000-1050 DEG C is warmed up to by the speed of 50-80 per hour DEG C, make potassium steel fully carry out austenitizing, insulation 2-3 hour, carrying out the water-tenacity treatment total processing time in water of then being quenched is 13-14 hour;
B () is when matrix is low-alloy high-tensile structural steel, its heat treatment step is: heat-treat at about 550-800 DEG C, matrix is pearlitic structrure, or, heat-treat at 220-550 DEG C, matrix is bainite structure, or, heat-treat below 220 DEG C, matrix is martensitic structure.
Described liner plate take steel alloy as matrix, selected steel alloy is potassium steel or low-alloy high-tensile structural steel, selected potassium steel matrix is ZGMn13-1, ZGMn13-2, ZGMn13-3, ZGMn13-4 or ZGMn13-5, see GB GB/T 5680-1998, after water-tenacity treatment, obtain single austenite structure.Selected low-alloy high-tensile structural steel matrix is Q345A, Q345B, Q345C, Q345D, Q345E, Q420A, Q460A etc., sees GB GB/T1951-2008.Matrix according to heat treating regime be not all in pearlite, martensite, ferrite, bainite, austenite and sorbite one or more.
After the present invention obtains the liner plate complex of alloy steel matrix+vanadium by casting, introduce outer carbon source, directly carbide coating can be formed on surface, the working position of liner plate in the mode adding thermal diffusion, it is metallurgical binding between coating and liner plate matrix, adhesion is very strong, and overcome non-metallurgical binding between existing hard particles and metallic matrix, adhesion is very weak, particle holds caducous problem, has increased substantially the mechanical property of coating.And the method is simple to operate, without the need to complex device, the liner plate of acquisition is functional.Different heat treatment modes, makes liner plate working surface and matrix position have different mechanical properties, meets the different performance requirement to various piece in actual production.Due to the formation of the accurate single-crystal ceramic layer of surface compact, this ceramic layer presents comparatively obvious accurate single crystal organization, shows as crystal boundary and reduces, affect the dislocation also corresponding minimizing of fracture toughness under light microscope, the sub boundary in generation increases, and effectively improves the anti-crack ability of this ceramic layer.Liner plate working surface has higher hardness HRC52-65, and relative wear resistance is 10-20 times of matrix.Described relative wear resistance is defined as: take matrix material as standard specimen, under same load, tested coating produces the relative wear resistance that ratio that wear extent and standard specimen produce wear extent is called coating, therefore be several times of matrix also referred to as the relative wear resistance of coating, following identical parameters examination criteria is identical with it.
This is due to V wherein
2c dense ceramic layers is as the criterion single crystal organization, chemical stability and wearability good, there is low-friction coefficient, high rigidity, low-surface-energy and low thermal conductiv-ity.And micron V on the other side
8c
7the hardness of ceramic layer can only reach HRC42-50, and its relative wear resistance is 6-10 times of matrix.
Accompanying drawing explanation
Fig. 1 casts front external carbon source (graphite paper or graphite powder) and the layout drawing of vanadium plate in sand mold;
The partial enlarged drawing that composite liner after Fig. 2 heat treatment and sample intercept.
Detailed description of the invention
Below the preferred embodiments of the present invention are described, should be appreciated that preferred embodiment described herein is only for instruction and explanation of the present invention, is not intended to limit the present invention.
Embodiment 1: the preparation method of liner plate, comprises the steps:
1, first prepare a vanadium plate 1, wherein the purity of vanadium should control 99.7%.Described vanadium plate 1 should first by surface treatment in addition, and step is as follows:
First step pickling, selects the hydrochloric acid of 300ml/L, rear running water;
Second step pickling, selects the hydrofluoric acid of 300ml/L, rear running water;
3rd step surface finish, selects 800 object Al
2o
3sand paper, finally uses alcohol ultrasonic cleaning.The THICKNESS CONTROL of described vanadium plate 1 is at 0.2mm.
2, according to liner plate size, CO is used
2waterglass hardened sand makes sand mold 2, and according to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, backing surface fixed outer carbon source 3 bottom sand mold accordingly, external carbon source 3 is graphite paper, and described graphite paper is more than three grades, purity 85%, thickness is 0.1mm.Then vanadium plate 1 is placed in backing surface bottom sand mold 2, itself and graphite paper are combined closely (as shown in Figure 1).
3, smelt steel substrate for molten steel 4, temperature controls at 1500 DEG C, and selected steel substrate is ZGMn13-1.
4, above-mentioned molten steel 4 is poured into above-mentionedly be placed with in the sand mold 2 of vanadium plate 1 and graphite paper, pouring temperature controls at 1500 DEG C, the duration of pouring is within 10 seconds, be advisable, after one minute, at hot topping, after room temperature cooling, after molten metal cooled and solidified, take out foundry goods, sand removal process, obtaining liner plate matrix is ZGMn13-1 matrix 4, and backing surface is the complex with vanadium plate.
5, the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere; be warming up to 1000 DEG C; programming rate controls at 7 DEG C/min; temperature retention time is 6h; finally cool to room temperature with the furnace; thus form gradient composite coating at backing surface, and liner plate matrix 4 is still ZGMn13-1 (Fig. 2).Described protection gas is argon gas, and gas flow is 5ml/min.
6, the surface of gained has the liner plate of gradient composite coating, single austenite structure is obtained after water-tenacity treatment, heat treatment step is: within 1 hour, be warmed up to 350 DEG C, then 1050 DEG C are warmed up to by the speed of 65 DEG C per hour, potassium steel is made fully to carry out austenitizing, be incubated 2 hours, carrying out the water-tenacity treatment total processing time in water of then being quenched is 13 hours.
As shown in Figure 2, gained carbide coating comprises V
2c dense ceramic layers, be as the criterion monocrystalline phase, and its crystallite dimension is 20 μm; Along coating longitudinal profile, its thickness is 7 μm, wherein V
2the volume fraction of C is 90%.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2micron V under C dense ceramic layers 5
8c
7dense ceramic layers 6, along coating longitudinal profile, its thickness is 15 μm, V
8c
7volume fraction be 75%, its crystallite dimension is 5 μm.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2c dense ceramic layers 5 and micron V
8c
7v under dense ceramic layers 6
8c
7with the fused layer 7 of matrix, along coating longitudinal profile, its thickness is 123 μm, wherein V
8c
7volume fraction be 20%, its crystallite dimension is 5 μm.Now, described carbide coating can be composite coating, by described accurate monocrystalline V
2c dense ceramic layers 5, micron V
8c
7dense ceramic layers 6 and V
8c
7form with the fused layer 7 of matrix, and distribution gradient successively, its gross thickness is 145 μm.Described liner plate matrix is austenite.Liner plate working surface has higher hardness HRC52, and relative wear resistance is 10 times of matrix.
Embodiment 2: the preparation method of liner plate, comprises the steps:
1, first prepare a vanadium plate 1, wherein the purity of vanadium should control 99.8%.Described vanadium plate 1 should first by surface treatment in addition, and step is as follows:
First step pickling, the phosphoric acid of 60ml/L, rear running water;
Second step pickling, the sulfuric acid of 200ml/L, rear running water;
3rd step surface finish, selects 1000 object Al
2o
3sand paper, finally uses alcohol ultrasonic cleaning.The THICKNESS CONTROL of described vanadium plate 1 is at 1mm.
2, according to liner plate size, sand mold 2 is made with precoated sand, according to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, backing surface fixed outer carbon source 3 bottom sand mold 2 accordingly, external carbon source 3 is graphite paper, and described graphite paper is more than three grades, purity is 99%, and thickness is 0.2mm.Then vanadium plate 1 is placed in backing surface bottom sand mold 2, makes itself and graphite paper combine closely (Fig. 1).
3, smelt steel substrate for molten steel 4, temperature controls at 1510 DEG C, and selected potassium steel base material is ZGMn13-2.
4, above-mentioned molten steel is poured in the above-mentioned sand mold being placed with vanadium plate 1 and graphite paper, pouring temperature controls at 1510 DEG C, the duration of pouring is within 20 seconds, be advisable, after one minute, at hot topping, after room temperature cooling, after molten metal cooled and solidified, take out foundry goods, sand removal process, obtaining liner plate matrix is ZGMn13-2 matrix 4, and backing surface is the complex with vanadium plate.
5, the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere; be warming up to 1050 DEG C; programming rate controls at 7 DEG C/min; temperature retention time is that 7h finally cools to room temperature with the furnace; thus form gradient composite coating at backing surface, and liner plate matrix 4 is still ZGMn13-2 (Fig. 2).Described protection gas is argon gas, and gas flow is 6ml/min.
6, the surface of gained has the liner plate of gradient composite coating, single austenite structure is obtained after water-tenacity treatment, heat treatment step is: within 1 hour, be warmed up to 300 DEG C, then 1000 DEG C are warmed up to by the speed of 50 DEG C per hour, potassium steel is made fully to carry out austenitizing, be incubated 2 hours, carrying out the water-tenacity treatment total processing time in water of then being quenched is 13 hours.
Described carbide coating comprises V
2c dense ceramic layers 5, be as the criterion monocrystalline phase, and its crystallite dimension is 22 μm; Along coating longitudinal profile, its thickness is 10 μm; Wherein V
2the volume fraction of C is 80%.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2micron V under C dense ceramic layers 5
8c
7dense ceramic layers 6, along coating longitudinal profile, its thickness is 50 μm, V
8c
7volume fraction be 78%, its crystallite dimension is 7 μm.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2c dense ceramic layers 5 and micron V
8c
7v under dense ceramic layers 6
8c
7with the fused layer 7 of matrix, along coating longitudinal profile, its thickness is 385 μm, wherein V
8c
7volume fraction be 60%, its crystallite dimension is 15 μm.Now, described carbide coating is composite coating, by described accurate monocrystalline V
2c dense ceramic layers 5, micron V
8c
7dense ceramic layers 6 and V
8c
7form with the fused layer 7 of matrix, and distribution gradient successively, its gross thickness is 445 μm.Described liner plate matrix is austenite.Liner plate working surface has higher hardness HRC60, and relative wear resistance is 14 times of matrix.
Embodiment 3: the preparation method of liner plate, comprises the steps:
1, first prepare a vanadium plate 1, wherein the purity of vanadium should control 99.8%.Described vanadium plate 1 should first by surface treatment in addition, and step is as follows:
First step pickling, the hydrogen peroxide of 120ml/L, rear running water;
Second step pickling, the hydrogen peroxide of 240ml/L, rear running water;
3rd step surface finish, selects 1000 object Al
2o
3sand paper, finally uses alcohol ultrasonic cleaning.The THICKNESS CONTROL of described vanadium plate 1 is at 0.35mm.
2, according to liner plate size, sand mold 2 is made with self-hardening resin sand, according to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, backing surface fixed outer carbon source 3 bottom sand mold 2 accordingly, external carbon source 3 is graphite paper, and described graphite paper is more than three grades, purity is 95%, and thickness is 0.35mm.Then vanadium plate 1 is placed in backing surface bottom sand mold 2, makes itself and graphite paper combine closely (Fig. 1).
3, smelt steel substrate for molten steel 4, temperature controls at 1520 DEG C, and selected steel substrate is ZGMn13-3.
4, above-mentioned molten steel 4 is poured into above-mentionedly be placed with in the sand mold 2 of vanadium plate 1 and graphite paper, pouring temperature controls at 1520 DEG C, the duration of pouring is within 30 seconds, be advisable, after one minute, at hot topping, after room temperature cooling, after molten metal cooled and solidified, take out foundry goods, sand removal process, obtaining liner plate matrix is ZGMn13-3 matrix, and backing surface is the complex with vanadium plate.
5, the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere; be warming up to 1080 DEG C; programming rate controls at 7 DEG C/min; temperature retention time is 9h; finally cool to room temperature with the furnace; thus form gradient composite coating at backing surface, and liner plate matrix 4 is still ZGMn13-3 (Fig. 2).Described protection gas is nitrogen, and gas flow is 7ml/min.
6, the surface of gained has the liner plate of gradient composite coating, single austenite structure is obtained after water-tenacity treatment, heat treatment step is: within 1 hour, be warmed up to 400 DEG C, then 1050 DEG C are warmed up to by the speed of 80 DEG C per hour, potassium steel is made fully to carry out austenitizing, be incubated 2 hours, carrying out the water-tenacity treatment total processing time in water of then being quenched is 13 hours.
Described carbide coating comprises V
2c dense ceramic layers 5, be as the criterion monocrystalline phase, and its crystallite dimension is 25 μm; Along coating longitudinal profile, its thickness is 12 μm; Wherein V
2the volume fraction of C is 95%.
Further, comprise and be positioned at above-mentioned accurate monocrystalline V
2micron V under C dense ceramic layers 5
8c
7dense ceramic layers 6, along coating longitudinal profile, its thickness is 55 μm, V
8c
7volume fraction be 80%, its crystallite dimension is 10 μm.
Further, can also comprise and be positioned at above-mentioned accurate monocrystalline V
2c dense ceramic layers 5 and micron V
8c
7v under dense ceramic layers 6
8c
7with the fused layer 7 of matrix, along coating longitudinal profile, its thickness is 659 μm, wherein V
8c
7volume fraction be 75%, its crystallite dimension is 15 μm.Now, described carbide coating is composite coating, by described accurate monocrystalline V
2c dense ceramic layers 5, micron V
8c
7dense ceramic layers 6 and V
8c
7form with the fused layer 7 of matrix, and distribution gradient successively, its gross thickness is 726 μm.Described liner plate matrix is austenite.Liner plate working surface has higher hardness HRC64, and relative wear resistance is 18 times of matrix.
Embodiment 4: the preparation method of liner plate, comprises the steps:
1, first prepare a vanadium plate 1, wherein the purity of vanadium should control 99.9%.Described vanadium plate 1 should first by surface treatment in addition, and step is as follows:
First step pickling, selects the phosphoric acid of 60ml/L, rear running water;
Second step pickling, the sulfuric acid of 200ml/L, rear running water;
3rd step surface finish, selects 1200 object Al
2o
3sand paper, finally uses alcohol ultrasonic cleaning.The THICKNESS CONTROL of described vanadium plate 1 is at 3mm.
2, according to liner plate size, sand mold 2 is made with tide mould sand, according to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, backing surface fixed outer carbon source 3 bottom sand mold 2 accordingly, external carbon source 3 is graphite powder, and described graphite powder selects granularity at 600 orders, and purity is 85%.Then vanadium plate 1 is placed in backing surface bottom sand mold 2, makes itself and graphite powder combine closely (Fig. 1).
3, smelt steel substrate for molten steel 4, temperature controls at 1530 DEG C, and selected steel substrate is Q345A.
4, above-mentioned molten steel 4 is poured in the above-mentioned sand mold being placed with vanadium plate and graphite powder, pouring temperature controls at 1530 DEG C, the duration of pouring is within 40 seconds, be advisable, after one minute, at hot topping, after room temperature cooling, after molten metal cooled and solidified, take out foundry goods, sand removal process, obtaining liner plate matrix is Q345A, and backing surface is the complex with vanadium plate.
5, the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere; be warming up to 1160 DEG C; programming rate controls at 7 DEG C/min; temperature retention time is 12h; finally cool to room temperature with the furnace; thus form gradient composite coating at backing surface, and liner plate matrix 4 is still Q345A (Fig. 2).Described protection gas is argon gas, and gas flow is 6ml/min.
6, the surface of gained has the liner plate of gradient composite coating, and by further heat treatment to obtain more suitably matrix, heat treatment step is: heat-treat at 220 DEG C, and matrix is martensitic structure.
Described carbide coating comprises V
2c dense ceramic layers 5, be as the criterion monocrystalline phase, and its crystallite dimension is 50 μm, and along coating longitudinal profile, its thickness is 25 μm, wherein V
2the volume fraction of C is 95%.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2micron V under C dense ceramic layers 5
8c
7dense ceramic layers 6, along coating longitudinal profile, its thickness is 90 μm, V
8c
7volume fraction be 80%, its crystallite dimension is 15 μm.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2c dense ceramic layers 5 and micron V
8c
7v under dense ceramic layers 6
8c
7with the fused layer 7 of matrix, along coating longitudinal profile, its thickness is 1095 μm, wherein V
8c
7volume fraction be 55%, its crystallite dimension is 20 μm.Now, described carbide coating is composite coating, by described accurate monocrystalline V
2c dense ceramic layers 5, micron V
8c
7dense ceramic layers 6 and V
8c
7form with the fused layer 7 of matrix, and distribution gradient successively, its gross thickness is 1210 μm.Described liner plate matrix is martensite.Liner plate working surface has higher hardness HRC65, and relative wear resistance is 20 times of matrix.
Embodiment 5: the preparation method of liner plate, comprises the steps:
1, first prepare a vanadium plate 1, wherein the purity of vanadium should control 99.7%.Described vanadium plate 1 should first by surface treatment in addition, and step is as follows:
First step pickling, selects the hydrochloric acid of 300ml/L, rear running water;
Second step pickling, the hydrogen peroxide of 240ml/L, rear running water;
3rd step surface finish, selects 800 object Al
2o
3sand paper, finally uses alcohol ultrasonic cleaning.The THICKNESS CONTROL of described vanadium plate 1 is at 0.2mm.
2, according to liner plate size, CO is used
2waterglass hardened sand makes sand mold 2, and according to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, backing surface fixed outer carbon source 3 bottom sand mold accordingly, external carbon source 3 is graphite powder, and described graphite powder selects granularity at 800 orders, and purity is 89%.Then vanadium plate 1 is placed in backing surface bottom sand mold 2, makes itself and graphite powder combine closely (Fig. 1).
3, smelt steel substrate for molten steel 4, temperature controls at 1540 DEG C, and selected steel substrate is Q420A.
4, above-mentioned molten steel 4 is poured in the above-mentioned sand mold being placed with vanadium plate and graphite powder, pouring temperature controls at 1540 DEG C, the duration of pouring is within 50 seconds, be advisable, after one minute, at hot topping, after room temperature cooling, after molten metal cooled and solidified, take out foundry goods, sand removal process, obtaining liner plate matrix is Q420A, and backing surface is the complex with vanadium plate.
5, the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere; be warming up to 1050 DEG C; programming rate controls at 7 DEG C/min; temperature retention time is 8h; finally cool to room temperature with the furnace; thus form gradient composite coating at backing surface, and liner plate matrix 4 is still Q420A (Fig. 2).Described protection gas is nitrogen, and gas flow is 7ml/min.
6, the surface of gained has the liner plate of gradient composite coating, and by further heat treatment to obtain more suitably matrix, heat treatment step is: heat-treat at about 750 DEG C, and matrix is pearlitic structrure.
Described carbide coating comprises V
2c dense ceramic layers 5, be as the criterion monocrystalline phase, and its crystallite dimension is 42 μm; Along coating longitudinal profile, its thickness is 20 μm; Wherein V
2the volume fraction of C is 80%.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2micron V under C dense ceramic layers 5
8c
7dense ceramic layers 6, along coating longitudinal profile, its thickness is 75 μm, V
8c
7volume fraction be 78%, its crystallite dimension is 14 μm.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2c dense ceramic layers 5 and micron V
8c
7v under dense ceramic layers 6
8c
7with the fused layer 7 of matrix, along coating longitudinal profile, its thickness is 1000 μm, wherein V
8c
7volume fraction be 60%, its crystallite dimension is 15 μm.Now, described carbide coating is composite coating, by described accurate monocrystalline V
2c dense ceramic layers 5, micron V
8c
7dense ceramic layers 6 and V
8c
7form with the fused layer 7 of matrix, and distribution gradient successively, its gross thickness is 1095 μm.Described liner plate matrix is pearlite.Liner plate working surface has higher hardness HRC57, and relative wear resistance is 12 times of matrix.
Embodiment 6: the preparation method of liner plate, comprises the steps:
1, first prepare a vanadium plate 1, wherein the purity of vanadium should control 99.9%.Described vanadium plate 1 should first by surface treatment in addition, and step is as follows:
First step pickling, selects the hydrogen peroxide of 120ml/L, rear running water;
Second step pickling, the hydrogen peroxide of 240ml/L, rear running water;
3rd step surface finish, selects 1200 object Al
2o
3sand paper, finally uses alcohol ultrasonic cleaning.The THICKNESS CONTROL of described vanadium plate 1 is at 1.5mm.
2, according to liner plate size, sand mold 2 is made with precoated sand, according to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, backing surface fixed outer carbon source 3 bottom sand mold 2 accordingly, external carbon source 3 is graphite powder, and described graphite powder selects granularity at 1000 orders, and purity is 99%.Then vanadium plate 1 is placed in backing surface bottom sand mold 2, makes itself and graphite powder combine closely (Fig. 1).
3, smelt steel substrate for molten steel 4, temperature controls at 1560 DEG C, and selected steel substrate is Q460A steel.
4, above-mentioned molten steel 4 is poured in the above-mentioned sand mold being placed with vanadium plate and graphite powder, pouring temperature controls at 1560 DEG C, the duration of pouring is within 10 seconds, be advisable, after one minute, at hot topping, after room temperature cooling, after molten metal cooled and solidified, take out foundry goods, sand removal process, obtaining liner plate matrix is low-alloy high-tensile structural steel Q460A, and backing surface is the complex with vanadium plate.
5, the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere; be warming up to 1100 DEG C; programming rate controls at 7 DEG C/min; temperature retention time is 10h; finally cool to room temperature with the furnace; thus form gradient composite coating at backing surface, and liner plate matrix 4 is still Q460A steel (Fig. 2).Described protection gas is nitrogen, and gas flow is 6ml/min.
6, the surface of gained has the liner plate of gradient composite coating, and by further heat treatment to obtain more suitably matrix, heat treatment step is: heat-treat at about 300 DEG C, and matrix is bainite structure.
Described carbide coating comprises V
2c dense ceramic layers 5, be as the criterion monocrystalline phase, and its crystallite dimension is 36 μm; Along coating longitudinal profile, its thickness is 18 μm; Wherein V
2the volume fraction of C is 95%.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2micron V under C dense ceramic layers 5
8c
7dense ceramic layers 6, along coating longitudinal profile, its thickness is 70 μm, V
8c
7volume fraction be 90%, its crystallite dimension is 12 μm.
Further, also comprise and be positioned at above-mentioned accurate monocrystalline V
2c dense ceramic layers 5 and micron V
8c
7v under dense ceramic layers 6
8c
7with the fused layer 7 of matrix, along coating longitudinal profile, its thickness is 982 μm, wherein V
8c
7volume fraction be 85%, its crystallite dimension is 15 μm.Now, described carbide coating is composite coating, by described accurate monocrystalline V
2c dense ceramic layers 5, micron V
8c
7dense ceramic layers 6 and V
8c
7form with the fused layer 7 of matrix, and distribution gradient successively, its gross thickness is 1070 μm.Described liner plate matrix is bainite.Liner plate working surface has higher hardness HRC62, and relative wear resistance is 16 times of matrix.
Comparative example 1, its preparation method is as follows: with laser cladding directly by V
8c
7the cladding of vanadium carbide particle, at the working face of liner plate, obtains coating, and thickness is 30 μm, and volume fraction is 80%, and the average microhardness of gained coating is 2200HV
0.1, relative wear resistance is 3.62 times of matrix.
In comparative example, Laser Surface Modification Technology production cost is high, and production efficiency is low, and technological parameter is wayward, and uses bonding agent will cause pore and slag inclusion in use procedure; And in composite bed, there is not accurate monocrystalline V
2c dense ceramic layers and micron V
8c
7dense ceramic layers, composite bed thickness and V
8c
7content is less, V
8c
7crystallite dimension is larger; Simultaneously, recombination process is only externally add the intergranular gap of hard vanadium carbide to carry out casting and blend and carry out melting, sintering to additional particle, non-metallurgical binding between hard vanadium carbide particle and metallic matrix, adhesion is very weak, particle easily comes off or there is oxidation, Inclusion Problem, therefore, its mechanical property is poor.
Last it is noted that the foregoing is only the preferred embodiments of the present invention, be not limited to the present invention, although with reference to previous embodiment to invention has been detailed description, for a person skilled in the art, it still can be modified to the technical scheme described in foregoing embodiments, or carries out equivalent replacement to wherein portion of techniques feature.Within the spirit and principles in the present invention all, any amendment done, equivalent replacement, improvement etc., all should be included within protection scope of the present invention.
Claims (21)
1. a liner plate, has wear-resistant coating on its surface, it is characterized in that: described wear-resistant coating is V
2c dense ceramic layers.
2. liner plate as claimed in claim 1, is characterized in that: V
2c dense ceramic layers is as the criterion monocrystalline phase, and described accurate monocrystalline refers to mutually, between polycrystalline phase and monocrystalline mutually between, compared to polycrystalline phase, uniform orientation is high, crystal boundary obviously reduces, and the microscopic structure that atomic arrangement is more orderly.
3. liner plate as claimed in claim 1 or 2, is characterized in that: along V
2c dense ceramic layers longitudinal profile, its thickness is 7-25 μm, is preferably 12-22 μm, is more preferably 15-20 μm; Preferably, wherein V
2the volume fraction of C is greater than 80%, is preferably greater than 90%; Preferably, V
2c crystallite dimension is 20-50 μm, is preferably 30-50 μm.
4. a liner plate, has gradient composite coating on its surface, it is characterized in that: described gradient composite coating is carbide coating, comprises the V of distribution gradient successively
2c dense ceramic layers, micron V
8c
7dense ceramic layers, V
8c
7with the fused layer of matrix.
5. liner plate as claimed in claim 4, is characterized in that: V
2c dense ceramic layers is as the criterion monocrystalline phase, and described accurate monocrystalline refers to mutually, between polycrystalline phase and monocrystalline mutually between, compared to polycrystalline phase, uniform orientation is high, crystal boundary obviously reduces, and the microscopic structure that atomic arrangement is more orderly.
6. the liner plate as described in claim 4 or 5, is characterized in that: along V
2c dense ceramic layers longitudinal profile, its thickness is 7-25 μm, is preferably 12-22 μm, is more preferably 15-20 μm; Preferably, wherein V
2the volume fraction of C is greater than 80%, is preferably greater than 90%; Preferably, V
2c crystallite dimension is 20-50 μm, is preferably 30-50 μm.
7. the liner plate as described in one of claim 4-6, is characterized in that: along micron V
8c
7dense ceramic layers longitudinal profile, its thickness is 15-90 μm, is preferably 40-88 μm, is more preferably 70-88 μm; Preferably, V
8c
7volume fraction be greater than 70%, be preferably greater than 75%; Preferably, V
8c
7crystallite dimension be 5-15 μm, be preferably 6-15 μm, be more preferably 8-15 μm.
8. the liner plate as described in one of claim 4-7, is characterized in that: along V
8c
7with the fused layer longitudinal profile of matrix, its thickness is 123 μm-1095 μm, is preferably 300-1069 μm; Preferably, wherein V
8c
7volume fraction be 20%-85%, be preferably 50%-85%; Preferably, V
8c
7crystallite dimension be 5-20 μm, be preferably 10-20 μm.
9. the liner plate as described in one of claim 4-8, is characterized in that: gradient composite coating gross thickness is 145-1210 μm, more preferably at 400-1180 μm.
10. the liner plate as described in one of claim 4-9, is characterized in that: organize according to heat treatment be not all in pearlite, martensite, ferrite, bainite, austenite and sorbite one or more; Preferably, this gradient composite coating is applied in steel alloy surface.
The preparation method of 11. 1 kinds of liner plates as described in one of claim 1-3, is characterized in that, backing surface has wear-resistant coating, comprises the steps:
1) first prepare a vanadium plate, preferably, wherein the purity of vanadium should control at 99.7-99.9%; More preferably, the THICKNESS CONTROL of described vanadium plate is at 0.2-3mm; Preferably, described vanadium plate is first by addition surface treatment;
2) sand mold is made according to liner plate size, according to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, accordingly backing surface fixed outer carbon source bottom sand mold, then vanadium plate is placed in backing surface bottom sand mold, itself and external carbon source are combined closely; Preferably, CO is used
2waterglass hardened sand, precoated sand, self-hardening resin sand or tide mould sand make sand mold;
3) steel alloy base material is smelted for molten steel;
4) poured into by above-mentioned molten steel in the above-mentioned sand mold being placed with vanadium plate and external carbon source, after molten steel cooled and solidified, take out foundry goods, sand removal process, obtaining bottom liner plate is alloy steel matrix, and liner plate upper surface is the complex with vanadium plate; Preferably, pouring temperature controls at 1500-1560 DEG C, and the duration of pouring is that 10-50 is advisable second; More preferably, after one minute, at hot topping; Further preferably, room temperature cooling.
5) the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere, finally cools to room temperature with the furnace, thus forms wear-resistant coating at backing surface, and liner plate matrix is still alloy steel matrix;
Wherein, wear-resistant coating is V
2c dense ceramic layers.
The preparation method of 12. liner plates as claimed in claim 11, is characterized in that: V
2c dense ceramic layers is as the criterion monocrystalline phase, and described accurate monocrystalline refers to mutually, between polycrystalline phase and monocrystalline mutually between, compared to polycrystalline phase, uniform orientation is high, crystal boundary obviously reduces, and the microscopic structure that atomic arrangement is more orderly; Preferably, by rate-determining steps 5) in temperature retention time, holding temperature obtain this V
2c dense ceramic layers.
The preparation method of 13. 1 kinds of liner plates as described in one of claim 4-10, is characterized in that, backing surface has gradient composite coating, comprises the steps:
1) first prepare a vanadium plate, preferably, wherein the purity of vanadium should control at 99.7-99.9%; More preferably, the THICKNESS CONTROL of described vanadium plate is at 0.2-3mm; Preferably, described vanadium plate is first by addition surface treatment;
2) sand mold is made according to liner plate size, according to the work force-bearing situation of liner plate, the position of its key wear is the upper surface of liner plate, accordingly backing surface fixed outer carbon source bottom sand mold, then vanadium plate is placed in backing surface bottom sand mold, itself and external carbon source are combined closely; Preferably, CO is used
2waterglass hardened sand, precoated sand, self-hardening resin sand or tide mould sand make sand mold;
3) steel alloy base material is smelted for molten steel;
4) poured into by above-mentioned molten steel in the above-mentioned sand mold being placed with vanadium plate and external carbon source, after molten steel cooled and solidified, take out foundry goods, sand removal process, obtaining bottom liner plate is alloy steel matrix, and liner plate upper surface is the complex with vanadium plate; Preferably, pouring temperature controls at 1500-1560 DEG C, and the duration of pouring is that 10-50 is advisable second; More preferably, after one minute, at hot topping; Further preferably, room temperature cooling;
5) the liner plate complex obtained having cast puts into the holding furnace inside holding with protective atmosphere, finally cools to room temperature with the furnace, thus forms gradient composite coating at backing surface, and liner plate matrix is still alloy steel matrix;
6) surface of gained have gradient composite coating liner plate, by further heat treatment to obtain more suitably matrix.
The preparation method of 14. liner plates as claimed in claim 13, it is characterized in that: by rate-determining steps 5) in temperature retention time, holding temperature obtain this gradient composite coating and carbide coating, described carbide coating comprises the accurate monocrystalline phase V of distribution gradient successively
2c dense ceramic layers, micron V
8c
7dense ceramic layers, V
8c
7with the fused layer of matrix.
The preparation method of 15. liner plates as claimed in claim 14, is characterized in that: in step 5) in holding temperature, temperature retention time and the gross thickness of gradient composite coating that finally can obtain meet following formula,
L＝kTlogt
1/2+b
0
Wherein:
The gross thickness (μm) of L---gradient composite coating,
K---be constant, value is 0-1, k ≠ 0,
T---holding temperature (K),
T---temperature retention time (s),
B
0---original depth (μm), the thickness of the composite bed formed after namely molten steel is poured into a mould and between vanadium plate.
The preparation method of 16. liner plates as described in one of claim 13-15, is characterized in that: described step 1) in, surface-treated step is as follows:
First step pickling, selects the hydrogen peroxide of the hydrochloric acid of 300ml/L or the phosphoric acid of 60ml/L or 120ml/L, rear running water;
Second step pickling, selects the hydrogen peroxide of the hydrofluoric acid of 300ml/L or the sulfuric acid of 200ml/L or 240ml/L, rear running water;
3rd step surface finish, selects 800-1200 object Al
2o
3sand paper, finally uses alcohol ultrasonic cleaning.
The preparation method of 17. liner plates as described in one of claim 13-16, is characterized in that: described step 2) in external carbon source be graphite paper or graphite powder; Preferably, described graphite paper is more than three grades, and purity is 85-99%, and thickness is 0.1-0.35mm; Preferably, described graphite powder selects granularity at 600-1000 order, and purity is 85-99%.
The preparation method of 18. liner plates as described in one of claim 13-17, is characterized in that: described step 5) in, be warming up to 1000-1160 DEG C, programming rate controls at 7 DEG C/min, and temperature retention time is 6-12h, preferred 8-10h.
The preparation method of 19. liner plates as described in one of claim 13-18, is characterized in that: selected alloy steel matrix is low-alloy high-tensile structural steel or potassium steel.
The preparation method of 20. liner plates as described in one of claim 13-19, it is characterized in that: described protection gas is argon gas or nitrogen, gas flow is 5-7ml/min.
The preparation method of 21. liner plates as described in one of claim 13-20, is characterized in that, preferably, with potassium steel or low-alloy high-tensile structural steel for matrix, described step 6) in heat treatment step be:
A () when matrix is potassium steel is, its heat treatment step is: after water-tenacity treatment, obtain single austenite structure, preferably, heat treatment step is: within 1 hour, be warmed up to 300-400 DEG C, then 1000-1050 DEG C is warmed up to by the speed of 50-80 per hour DEG C, make potassium steel fully carry out austenitizing, insulation 2-3 hour, carrying out the water-tenacity treatment total processing time in water of then being quenched is 13-14 hour;
B (), when matrix is low-alloy high-tensile structural steel, its heat treatment step is: heat-treat at about 550-800 DEG C, and matrix is pearlitic structrure; Or heat-treat at 220-550 DEG C, matrix is bainite structure; Or heat-treat below 220 DEG C, matrix is martensitic structure.
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