CN105132791B - A kind of abrasion-proof alloy of improvement - Google Patents
A kind of abrasion-proof alloy of improvement Download PDFInfo
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- CN105132791B CN105132791B CN201510382089.7A CN201510382089A CN105132791B CN 105132791 B CN105132791 B CN 105132791B CN 201510382089 A CN201510382089 A CN 201510382089A CN 105132791 B CN105132791 B CN 105132791B
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- 229910001037 White iron Inorganic materials 0.000 claims abstract description 92
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 88
- 239000011651 chromium Substances 0.000 claims abstract description 82
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 76
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- 229910052799 carbon Inorganic materials 0.000 claims description 26
- 229920001296 polysiloxane Polymers 0.000 claims description 24
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- 239000011572 manganese Substances 0.000 claims description 20
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- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 11
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- 229910052742 iron Inorganic materials 0.000 abstract description 9
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Landscapes
- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
Abstract
A kind of anti-wear high chromium white iron, the white iron has a kind of micro-structural in the case of without Overheating Treatment, and austenite and M are contained in micro-structural7C3Carbide, contain at least one martensite promoter and at least one austenite stabilizer in the white iron, and the content of the martensite promoter and austenite stabilizer reach respective level so that between the two effect balance so that white iron do not exist crackle.The white mouth iron can be used to casting or being formed the deposited surface of hardening weldering.
Description
Divisional application
The present invention is the divisional application of the application for a patent for invention of Application No. 200480044720.2.The applying date of original application
It is on October 27th, 2004, Application No. 200480044720.2, entitled " a kind of abrasion-proof alloy of improvement ".
Technical field
It is suitable to parts surface hardening the invention belongs to the technical field of abrasion-proof alloy, particularly one kind, can also carries out into
Product direct pouring, the white iron of the anti-wear high-chromium amount that its fracture toughness is improved.
Background technology
White iron containing chromium, particularly high chromium white iron, due to containing hard M7C3Carbide, with very strong anti-wear
Property, M is Fe, Cr or Cr, Fe here, but is likely to containing a small amount of other elements such as Mn or Ni according to composition, this anti-wear
High chromium white iron may be hypoeutectic, eutectic or hypereutectic state.
The phosphorus content of hypoeutectic high chromium white iron is up to 3.0%.Contain in its microstructure and be present in M7C3Carbide
With the tree-shaped crystalline substance of primary austenite in austenite eutectic mixture matrix.The phosphorus content of eutectic white pig iron is 3.0%-4.0%,
Its microstructure is M7C3The eutectic mixture of carbide and austenite.The phosphorus content of hypereutectic white iron is 3.5%-5.0%,
Its microstructure contains and is present in M7C3Nascent M in carbide and austenite eutectic mixture matrix7C3Carbide.Every kind of feelings
Under condition, exactly M7C3Carbide, as eutectic carbide or primary carbide, makes this alloy have anti-wear characteristic.It is hypereutectic
White iron contains more hard antiwear M compared with hypoeutectic white iron7C3Carbide, therefore frequent turning into carries out hardening weldering
Deposited first-selected alloy.However, hypereutectic white iron is generally unsuitable for casting, the crackle that reason is produced when being cooling causes stress to produce
It is raw.
In general, if improving the anti-wear characteristic of hypereutectic high-chromium white iron, its fracture toughness will drop therewith
It is low.Chromium white iron high is widely used in that anti-wear property requirement is high and the relatively low mining of fracture toughness relative requirement and mineral products add
Industry.However, other application requirement materials have fracture toughness higher, this means that hypereutectic white iron can not be applied
In these occasions, to solve this problem, people have done different trials.
The background technology of Australian Patent AU-A-28865/84 relates generally to the height of hypoeutectic and hypereutectic mixture
Chromium white iron, it describes the experiment of multiple failure, it is intended to be made the suitably cast mistake for having wear resistance and fracture toughness concurrently
Eutectic white pig iron alloy, AU-A-28865/84 is also illustrated and tested several times simultaneously, it is intended to is made and is had wear resistance concurrently and be broken tough
Property hypoeutectic synthetic and be suitable to the deposited alloy of hardening weldering.However, AU-A-28865/84 is actually mainly mixed by casting
Synthesis shape solves the crack problem of cast iron mixture, that is, a kind of particular alloy and matrix are carried out into metallurgical binding, then
Eliminated when alloy is cooled down and the possibility of crackle occur, eventually form cast iron mixture.Really, AU-A-28865/84 attempts to lead to
Cross the M for ensureing that the main component in cast iron mixture is not more than 75 microns for sectional dimension7C3Carbide is more than solving phosphorus content
The low fracture toughness and crack problem of 4.0% hypereutectic cast iron, also advise number of mechanisms to do this trial.So, AU-A-
28865/84 purpose is by forming blending constituent with main component M in limitation alloy7C3The size of carbide carrys out solve problem.
United States Patent (USP) 5,803,152 attempts the micro-structural of refining hypereutectic white iron, especially thick hypereutectic white iron
Micro-structural, the nucleation amount of main component carbide is reached maximum, the fracture toughness and wear resistance of material are increased with this.Essence
Refining is exactly to add a kind of special metal, this metal will therefrom to inhale in the toppling process that molten metal fluid is cast
Heat is received, and supercooling is carried out to fusing metal, so as to make it into the first curdled appearance between liquid and solid state temperature.
As attempting improving the fracture toughness of hardfacing alloy in the past, United States Patent (USP) 6,375,895 is pointed out, although thing
First made precautionary measures, but in many formerly technologies, case-hardened high chromium white iron always have in the weld state or it is many or
Few dense crackle net occurs.The proposition of United States Patent (USP) 6,375,895, the austenitic matrix (about 300BHN~600BHN) of softening
The hardness of middle primary carbide (about 1700 Brinell hardness (BHN)) reach can cause afterwards to a certain degree metal from molten state cool down when
There is contraction crack.The solution of United States Patent (USP) 6,375,895 is using a kind of special alloy mixture, in Surface hardened layer
The matrix of preceding preheated mixture, then cools down whole mixture, this can ensure in micro-structural all the time with the presence of martensite simultaneously
And whole alloy rigidity is consistent (about 455BHN~512BHN).
It is an object of the invention to provide anti-wear Gao Ge that is a kind of suitably cast and being used as flawless hard alloy
White iron.This high chromium white iron need not generate blending constituent also without complicated foundry engieering when being cast, meanwhile,
When carrying out Surface hardened layer, it is not required that carry out the pre-add heat treatment of costliness.
Before introducing the present invention, the formerly description of technology is only background technology explanation first more than statement, first to these
The reference of technology be not offered as these patent-related documents Australia or disclose elsewhere and enter public information
Scope.
The content of the invention
The present inventor illustrates the reason for anti-wear high chromium white iron fracture toughness is low first.Inventor has found M7C3Carbon
There is a thin layer martensite in compound and austenite interface, this thin layer martensite causes or at least triggered crackle.This is right
Situations below is applicable：M7C3Carbide is primary carbide, and austenite is in eutectic matrix；Or M7C3Carbide is eutectic carbon
Compound, austenite is eutectic austenite；Or M7C3Carbide is eutectic carbide, and austenite is primary austenite.So, the hair
Hypoeutectic, eutectic and the hypereutectic high-chromium white iron of casting are now can be applied to, the discovery can also be applied to the eutectic and mistake of welding
Eutectic alloy and many (being such as not all of) hypoeutectic alloy.
In addition, inventor determines that this usual thickness of martensite thin layer may be one to several microns, it is also possible to only several
Individual nanometer.This thin layer may not be continuously to be likely to variable thickness cause completely around carbide, and certain this thin layer is also only
Can be just observed that under the instruments such as electron microscope.
The discovery is pointed out, in high chromium white iron, due to M7C3Carbide and austenite the adjoining chromium at position and subtracting for carbon
It is few, result in the formation of thin layer martensite.The discovery also indicated that, M can be caused containing silicon in composition7C3Carbide and neighbouring Austria
Martensite is generated between family name's body.
The discovery points out that Material shrinkage during due to being cooled down after deposited metal solidification, the weldering that hardening weldering is generated when applying applies internal
Portion can produce tensile residual stresses.It was found that in also indicate that, with M7C3This layer of neighbouring thin, hard and fragility martensite of carbide
These tensile stress can be discharged by crackle, if without this layer thin martensite, softer austenite can then absorb these remnants
Stress is deformed, which prevent crackle generation and micro-crack extension degree is reduced to minimum.
Inventor also found, in M7C3The martensite that carbide and austenite interface are present is not to cast and harden weldering to apply
In cause the sole cause that crackle produces, more chief reason (will be described in more detail below) is the M in material7C3Carbide Phases
The degree that connects is very high, and adding some alloys can improve M7C3The interconnection degree of carbide.This alloy additive effect is very
Greatly, addition one of which alloy can just make material supercooling before solidification, and this can be applied to cast and weld apply, when Connected degree high
M7C3Carbide be located at M7C3Martensite between carbide and austenite simultaneously in the presence of, the generation of crackle and expand just
Unavoidably.Work as M7C3The connection high of carbide occurs in the alloy, and these alloys are difficult martensite occur in adjacent surface
When, although the root of crackle can be avoided, but crackle generation and extension generally speaking in material are still inevitable.
Inventor points out, in most cases, no matter is applied to casting or welds apply, crackle in solution high chromium white iron
Generation and the method for expanding all are identicals.
The invention provides a kind of anti-wear high chromium white iron, the white iron without Overheating Treatment has a kind of micro- knot
Structure, contains austenite and M in micro-structural7C3Carbide, contains at least one martensite promoter and at least in the white iron
Austenite stabilizer is planted, and the martensite promoter and austenite stabilizer content are appropriate, and effect reaches balance, makes described
White iron without Overheating Treatment has a kind of micro-structural, and the micro-structural has following at least one feature：
I) in austenite and M7C3Do not exist martensite on carbide interface；With
Ii) the interconnection degree between its Carbide Particulate has a relatively low level；
The white iron does not exist crackle.In most cases, this white iron not only flawless and with preferably disconnected
Split toughness.
Have a kind of form, white iron is in as-cast condition, the content of martensite promoter and austenite stabilizer it is appropriate and
Effect is balanced up to cause, so that M in white iron7C3Do not exist martensite on interface between carbide and austenite.
Another form, white iron contains the hardened surface that the matrix after being applied through weldering is provided, and the hardened surface flawless is deposited
.Martensite promoter and austenite stabilizer effect make the M in micro-structural up to causing to balance7C3In carbide, its carbide is micro-
The interconnection degree of intergranular reaches a relatively low level, so, does not exist branch's carbonized particles in micro-structural, and described
The content of martensite promoter and austenite stabilizer suitably up to causing to balance, makes white iron in austenite and M7C3The boundary of carbide
Completely without martensite on face.
The invention provides a kind of M7C3In the absence of the anti-wear high chromium white iron of martensite on carbide and Austenite Interfacial
No matter by casting or conformal into hardened surface by weldering alloy, the alloy is, all completely without crackle.However, should be clear and definite
, there is no martensite can not exclude the possibility beyond interface inside austenite with the presence of martensite on above-mentioned interface
Property.The characteristics of invention is in M7C3Martensite thin layer will not be formed on carbide and austenite interface, rather than in other areas
Domain also excludes the possibility of martensite presence.In fact, in some compositions, there must be depositing for some martensites beyond interface
.
Another form, the invention provides a kind of anti-wear high chromium white iron, wherein at least one martensite promoter
Effect balance is sufficiently achieved with least one austenite stabilizer, has made M7C3Do not exist geneva on carbide and Austenite Interfacial
Body, thus white iron it is cast or by weldering it is conformal into hardened surface all without cracking.
One of alloying element silicon is exactly a kind of martensite promoter, and it can promote the generation of martensite, this combination gold dollar
Element also includes boron.In high chromium white iron of the invention, silicon is most important martensite promoter, can be with least one austenite
Stabilizer reaches required balance.However, boron can also be used as a kind of martensite promoter, when using content can reach 1% or
Even as high as 2%.Adding boron can influence the activity of silicon, and boron also can be used as single martensite promoter.In general, boron also may be used
As martensite promoter, but the control implemented in the present invention is primarily directed to the silicon as martensite promoter and at least one
Plant austenite stabilizer.
One of alloying element should be used as at least one austenite stabilizer, and its effect is to promote the life with stable austenite
Into.This combination gold element includes manganese, nickel, copper and molybdenum, and these elements can be used alone also to can be combined and use, in four kinds of elements, manganese
It is especially notable with nickel effect in the present invention.Although also providing a small amount of other austenite stabilizers of at least one in invention,
The control that the present invention is implemented is primarily directed to the manganese and/or nickel as austenite stabilizer.Equally, it should it is clear that, also may be used
Replace manganese and/or nickel using other austenite stabilizers.
In the present invention preferably scheme, the appropriate austenite stabilizer (such as manganese or nickel) that different alloying elements is constituted
Reached " sufficient effect balance " with martensite promoter (such as silicon or boron), it is suppressed that M7C3Carbide and Austenite Interfacial start
The generation of family name's body thin layer.This " the sufficiently balance " that these appropriate alloying elements reach present in high chromium white iron makes material
Material will not generate crackle when casting or hardening and weld and apply.
Further study these alloying elements, it has been proposed that using martensite promoter (such as silicon) as some high chromium white iron
Additive, to improve melt fluidity when its hardening weldering is applied or cast.But, the inventors discovered that, martensite promoter is (such as
Silicon) presence can produce the presence of the result of quite unexpected accumulative deterioration, martensite promoter to be produced to austenite stabilizer
Raw negative impact simultaneously causes the generation of martensite, therefore, martensite promoter is more than promoting the generation of martensite, Er Qiegeng
Plus can promote in austenite and M7C3The generation of carbide interface Markov body, here it is martensite promoter (such as silicon) and Austria
The reason for family name's body stabilizer will reach " sufficiently balance ".
Although silicon can promote martensite to generate, the content of silicon should increase or be maintained at certain level, because
The use of austenite stabilizer can offset the effect of martensite promoter.In other words, although the presence of silicon, fusing stream is being improved
Dynamic property aspect has good result, but austenite stabilizer still has to reach the level of abundance, and this can be by the metallographic that commonly uses
Technology is proved.In finding to there is martensite to generate the high chromium white iron being suppressed, the micro- photograph obtained using Metallographic Techniques
The mainly primary austenite of hypoeutectic iron shown in piece and eutectic matrix and the nascent M of hyper-eutectic irons7C3Carbide is together
Brilliant matrix, it was concluded that, austenite and M are contained in eutectic thing7C3Carbide, without martensite.For hypoeutectic white iron
Tree-shaped crystalline substance for, it is main it is tree-shaped it is brilliant all by austenite constitute or austenite in some regions also contain martensite, latter
In the case of kind, if martensite is included in austenite, these regions for containing martensite are acceptable.No matter which kind of feelings
Condition, the result that microphoto shows is identical with estimated, and the crackle occurred in photo is also satisfactory and can be solved with residual stress
Release, without further looking at.
It has been observed that we have found that despite the presence of austenite stabilizer, silicon also can be to promote martensite generation, in M7C3
When generating martensite on carbide and Austenite Interfacial, this facilitation is harmful, and these interfaces are probably eutectic phase
The group of carbide and austenite or primary austenite and eutectic carbide or primary carbide and eutectic austenite or these situations
Close.
In order to increase mobility when material is cast or welded deposited, the silicone content of certain level is needed in material.However,
Silicon is added not only for this purpose is reached, a kind of sufficient austenite stabilizer is added nor only for offset silicon conduct
The negative effect produced during martensite promoter a, factor is that addition austenite stabilizer can increase cost, however, more important
, silicon can produce complicated influence to the micro-structural of material.We have found that, according to the difference of silicone content, silicon can be strengthened
Or reduce M7C3The interconnection degree of carbide, this major embodiment in hypereutectic white iron, but it is also suitable for hypoeutectic spoken parts in traditional operas
Iron.
High chromium white iron " feature is partly pointed out in ASM handbooks volume 15 " casting " the 9th edition page 681 entitled " high chromium white iron "
It is have hard relatively discontinuous M7C3Eutectic carbide ".There is large-scale nascent M in hypereutectic white iron7C3The hexagonal of carbide
Bar, and these hexagonal bars are discontinuous.However, it is pointed out that silicon can influence eutectic carbide inside and nascent carbonization
The degree that Carbide Phases inside thing connect, increases M7C3The interconnection degree of carbide can increase the overall fragility of material,
Promote crackle generation and expand, conversely, reducing M7C3The interconnection degree of carbide contributes to hard austenite phase limitation to split
The generation and expansion of line.
Silicon can increase supercooling phenomenon during molten state before material solidification, and so, silicon increased eutectic M7C3Carbide
Interconnection degree, and for hypereutectic micro-structural, silicon increased nascent M7C3The interconnection degree of carbide.Meanwhile,
Therefore overall fragility when material is cast or welded deposited also increase.However, if the content of silicon can be controlled, supercooling is just not
Can occur.Research finds that silicon can also reduce nascent M7C3Carbide and eutectic M7C3The interconnection degree of carbide, so
Fracture toughness, wear resistance and the thermal-shock resistance of material can be improved.Silicone content is total to during hypoeutectic mixture can be reduced when higher
Brilliant M7C3The interconnection degree of carbide, the eutectic structure for being so connected with each other degree complicated rule higher will not be in eutectic
Formed in alloy.
Research finds, determines to be considered as another factor during silicone content, especially in casting, at present, casting high chromium white
Using slower cooling velocity during iron.Page 683 " knockout " partly has described below in above-mentioned ASM handbooks：" by metal in fusing shape
Be cooled under state room temperature can Crack prevention generation, especially cooling final stage martensite generate when.", the part is further
Point out, carry out the measure that should force to take this pre- Anti-cracking generation when heavy mail casts, frequently produce high residual stress and crackle
The reason for be that temperature is too high when casting is separated with mould, in other words, the generational verctor of crackle is relevant with cooling velocity, slower
Cooling velocity can reduce the generation and expansion of crackle.
It was found that because at least one martensite promoter (such as silicon) and at least one austenite stabilizer have reached effect
Should balance, increasing silicone content can improve cooling velocity and will not crack, and this is certainly in terms of the Foundry Production cycle is shortened
It is highly advantageous.However, the discovery is also applied for the welding just higher of original cooling velocity, because the silicon of high level can pass through
Release residual stress reduces the probability of crackle generation, and silicone content and cooling velocity need not be considered to M7C3Carbide Phases are interconnected
Connect the combined effect of degree.
Consider factors above, the silicone content in high chromium white iron of the present invention should be 0.25%~3.5%, however, silicone content
It is more preferable when between 0.5%~3.25%.(determined by micro-structural) in some forms, silicone content should not be greater than 2.75%, after
Face chapters and sections have relevant explanation.In a way, the effect of boron is more more effective than silicon, and as previously discussed, the content of boron is required nothing more than most
High about 1% or about 2%.
All parameters, unless stated otherwise, are weight percentage.Be applied to hardening weldering apply when, the ratio can be by matrix
Metal dilution, such as allowed band are 10%~40%.
In scheme of the invention first-selected, containing austenite stabilizer manganese and nickel in alloy, content is 4.0%~
12%.Such as in order to prevent austenite to be converted into martensite, its content should be 4.0%~8.0%.However, it should be clear that closing
Two kinds of elements need not simultaneously be contained in gold, because simply by the presence of a kind of element, and content is in scope mentioned above, so that it may
To meet requirement.Equally, although in some cases, the content of manganese and/or nickel in some alloys may be up to about 12%, most
Good scope should be 4.0%~8.0%.
When using copper as austenite stabilizer, its consumption is identical with above-described manganese and/or nickel.However, the use of molybdenum
Amount needs increase, because a part of molybdenum is required to generate carbide, and this part molybdenum will cannot function as austenite stabilizer and use.This
Sample, it is contemplated that using a kind of substitute of molybdenum as the alloy addition for having similar austenite stabilization.However, we are also
It is to recommend copper and molybdenum both elements, but when using, its content will be in reduced levels, and be used with reference to manganese and/or nickel.Consider
To Cost Problems, this method is particularly true for molybdenum.
Here recommend, two or more austenite stabilizer may be used in combination, and austenite stabilizer always contains
Amount should be no more than 20%, preferably not more than 16%.
Reach the balance of application claims, it is necessary to control some variables, these variables include silicone content, manganese content and nickel
Content.If manganese and nickel can be exchanged, two contents can take a variable as, however, their effects as austenite stabilizer
Really some slight difference, thus it is more preferable as independent variable.4th variable is cooling velocity, used as a variable, cooling
Speed is relative larger with the relation of casting, because in the case where weldering is applied, the scope of cooling velocity is limited.
Present case shows, we can empirically established above-described four variables relation.However, current institute
Empirical relation that is knowing or having used, such as determines martensite start temperature MsAndrew (Andrew) relation, all with reach this
The required balance of invention is unrelated, therefore, the form of four relationship between variables is indefinite.It is final as a result, for giving
For determining the high chromium white iron of carbon and chromium content, it is necessary to carry out preliminary test casting and preliminary test weldering is applied, so just can determine that
The balance that silicon and manganese and/or nickel should reach, cooling velocity when these experiments are implemented should be with the production of whole spoken parts in traditional operas ferrous components
Operation is relevant.Equally, at least in these trials, silicone content should be determined in advance can't cause sub-cooled, so, by adjusting
The content of section manganese and/or nickel will be reduced come the test number (TN) of balance needed for reaching.
In preliminary test, we can be decided whether to reach by a magnet in casting or the deposited examination body of weldering with this
Required balance, if ferromagnetism (being used to indicate martensite whether there is herein) is not obvious, this balance may be substantially
Reach.But, M is determined using metallographic detection7C3Carbide and Austenite Interfacial are then more particularly suitable with the presence or absence of martensite.
In high chromium white iron of the invention, chromium content is typically recommended as 8%~50%, and optimal is 10%~30%.Carbon contains
Amount is general 1.0%~6.0%.However, the content of carbon have some overlap subrange, this be decided by white iron be hypoeutectic,
Eutectic or hypereutectic state.Carbide is mainly M7C3Form, a small amount of hardness phase is also likely to be present in regions such as primary austenites
To relatively low M23C6Carbide.
Carbon content is generally 1.0%~3.0% in hypoeutectic chromium white iron, and carbon content is generally in eutectic chromium white iron
3.0%~4.0%, and carbon content is generally 3.5%~5.0% in hypereutectic chromium white iron.If these scopes can change
More preferably, this is decided by whether there is other alloying elements in material.For example, the total content of niobium and/or vanadium is up in material
When about 10% (add both elements can generate Niobium carbide and vanadium carbide, to improve wear resistance), hypoeutectic, eutectic
Content with the carbon in hypereutectic state can make the following changes：
Hypoeutectic 2.0%~4.0%
Eutectic 4.25%~4.75%
Hypereutectic 5.0%~6.0%
These scopes also have more changes, and this is decided by the difference of contained alloying element.It is proficient in the people of this technique
The change of clear and definite these scopes is occurred and how occurred by member under what conditions, and this has done relevant explanation in Fig. 1.
Brief description of the drawings
For convenience of the present invention is understood, accompanying drawing is referred to：
Fig. 1 is chromium white iron liquidus curve perspective view commonly used at present；
Fig. 2 is the displaing micro picture of sample drawn from the hypereutectic body of casting according to current test form；
Fig. 3 is the displaing micro picture of Fig. 2 subregions, and multiplication factor becomes big；
Fig. 4 is the displaing micro picture of Fig. 2 subregions, and multiplication factor is bigger；
Fig. 5 is the displaing micro picture of present invention sample drawn from the hypereutectic body of casting of chromium white iron；
Fig. 6 is identical sample displaing micro picture in Fig. 5, and multiplication factor becomes big；
Fig. 7 is the crackle shooting figure on the typical deposited surface of prior art hardening weldering in sample I；
Fig. 8 (a) and (b) are the displaing micro picture of sample shown in Fig. 7；
Fig. 9 is the displaing micro picture using the sample II of prior art hardened surface, it is shown that preferable but unrepresentative
Micro-structural；
Figure 10 is the displaing micro picture using the sample III of prior art hardened surface, it is shown that typical but bad is micro-
Structure；
Figure 11 (a) and 11 (b) are the displaing micro picture being each exaggerated, and display crackle spreads all over bad micro- knot of Fig. 9 samples II
Structure；
Figure 12 and Figure 13 are the displaing micro picture for showing Figure 10 samples bad micro-structurals of III respectively；
Figure 14 is the electron microscopic picture of Figure 10 samples III, it is shown that the bad microstructure features of typical case；
Figure 15 is the deposited shooting photo of typical high chromium white iron weldering of the invention；
Figure 16 is the displaing micro picture along welding bead longitudinal cross-section shown in Figure 15；
Figure 17 is the displaing micro picture along welding bead lateral cross section shown in Figure 15.
Specific embodiment
Fig. 1 is that the liquidus curve of Fe-Cr-C of the high chromium white iron metastable state C-Cr-Fe liquid phases surface rich in mono- jiao of Fe is thrown
Shadow figure.Carbon content is up to 6% in this three metamember, and chromium content is up to 40%, while also containing a small amount of manganese and silicon.
Liquidus curve perspective view in Fig. 1 is shown the relation of micro-structural and carbon chromium content.The region representation for indicating γ is sub-
The composition of point A, B, C, D and E point is referred to as a group I in eutectic composition, general range.
Composition A and B is close to boundary line in hypoeutectic region.Eutectic micro-structural is present in from U1To U2Straight line on,
From the composition near B along U1To U2Straight line to point C.Hypereutectic composition is indicating M7C3Region in, comprising components D and E.
It is any have promotion austenite should all be avoided to the methods for cooling of martensitic transformation function, for some compositions,
Preferably with a methods for cooling that martensite will not be promoted to generate.However, as previously discussed, can be reached when silicone content is higher
Cooling velocity higher.
Embodiment is described in detail
Illustrative blanket embodiment Table I for casting or welding deposited high chromium white ferrous components of the invention
Represented with Table II.Table I is group I compositions, comprising the composition that point A, B, C, D and the E shown in Fig. 1 are represented.Table II is to be similar into
Divide (concrete reason is described in detail above), because different comprising niobium and/or vanadium.
Table I-group I composition ranges
| Micro-structural | C% | Cr% | Nb/V% | Mn% | Ni% | Si% |
| Hypoeutectic | 1.0~3.0 | 18.0~27.0 | - | 4.0~8.0 | 4.0~8.0 | 0.25~2.75 |
| Eutectic | 3.0~4.0 | 15.0~27.0 | - | 4.0~8.0 | 4.0~8.0 | 0.25~2.75 |
| It is hypereutectic | 4.0~5.0 | 20.0~27.0 | - | 4.0~8.0 | 4.0~8.0 | 0.25~3.25 |
Table II-group II composition ranges
| Micro-structural | C% | Cr% | Nb/V% | Mn% | Ni% | Si% |
| Hypoeutectic | 2.5~4.0 | 18.0~27.0 | 10.0 | 4.0~8.0 | 4.0~8.0 | 0.25~2.75 |
| Eutectic | 4.25~4.75 | 15.0~27.0 | 10.0 | 4.0~8.0 | 4.0~8.0 | 0.25~2.75 |
| It is hypereutectic | 5.0~6.0 | 20.0~27.0 | 10.0 | 4.0~8.0 | 4.0~8.0 | 0.25~3.25 |
Note：
1. in the scope in Table I and Table II, the balance of composition is iron and incidental impurities, however, can as above add
Alloying element.
2. in the scope of Table II, the content up to 10% of niobium and vanadium, best total content is 10%.Similarly, since increasing
Plus niobium and/or vanadium, it is necessary to increase the carbon content that it is as shown in the table, to produce carbide.
Embodiment --- casting
From in industrial high chromium white cast iron casting body, the micro-structural of the material to be analyzed in one section of cutting as sample
Feature.This section of high chromium white iron can be used the method cutting of water spray grinding and cutting to obtain, and use a thin diamond dust rotating disk (circular disc)
Sample is cut out from this section of high chromium white iron, is cooled down using the sufficient water as coolant during cutting, use 500 times
Or more Olympus (Olympus) reflected light microscope of multiplication factor detect the sample, the sample is in non-etched and etching
It is detected under state, etchant is sour iron chloride (5 grams of FeCl3, 10 milliliters of HCL and 100 milliliter of H2O)。
Fig. 2 be industrial body of casting sample it is polished and through sour iron chloride etch after displaing micro picture.Region in Fig. 2 is
The crosspoint of subsurface flaws and face crack, these large-scale crackles are produced when may be cooled down after body of casting solidification.Crackle it
Between the crosspoint left side shoot same area high-resolution displaing micro picture it is as shown in Figure 3.
The micro-structural of Fig. 2 and Fig. 3 represents that the industrial body of casting is in casting state.The industrial body of casting chromium that Fig. 2 and Fig. 3 are represented is white
Mouth iron is hypereutectic structure, as shown in Table III.
Table IIIIndustrial body of casting composition %
| C | Mn | Si | Ni | Cr | Mo | Cu | Fe/ impurity |
| 4.5 | 1.90 | 0.49 | 0.12 | 34 | 0.95 | 0.07 | Balance |
Such as Fig. 2 and Fig. 3, be can see under respective multiplication factor, only nascent M in micro-structural7C3Carbide and Ovshinsky
Body.Although white iron composition is similar to, micro-structural here is significantly different with common high chromium white iron, in Fig. 2 and Fig. 3, Ovshinsky
Do not have well-regulated M in vivo7C3Eutectic carbide, for the eutectic thing of rule, the conference long of eutectic phase promotes the generation of the second phase.
The reason for occurring this different is believed to be the inoculation used in the industrial body of casting of production, and the effect of inovulant then makes
M7C3Assemble when carbide solidifies, the strength for driving carbide to grow up makes the carbide in austenite independently solidify enough, thus it is raw
Into divorced eutectic.
Micro-structural in Fig. 2 and Fig. 3 contains the nascent M in eutectic micro-structural is separated7C3Carbide (white), it is to avoid
Regular texture be connected with each other with carbide bar, complicated, it is favourable that this is produced for Crack prevention, because high chromium white
The crack path that iron casting or weldering are produced when applying is along M7C3Carbide and austenite interface, the complex rule of interconnection
Eutectic carbide structure provides the continuous path of length for crack growth, therefore, it is necessary to eliminate this structure.Although however,
Body of casting micro-structural in Fig. 2 and Fig. 3 has reached the purpose, and crackle can still occur, and reason can be learnt from Fig. 4.
Fig. 4 of high-amplification-factor shoots the top in the crackle crosspoint in Fig. 2, the right of vertical crack.In Fig. 4, light color
It is mutually nascent M7C3Carbide, accounts for leading deep base to separate eutectic austenite.However, in austenite and M7C3Carbide
, there is one layer of martensite in austenite boundaries region in interface, is indicated with black arrow.Equally, it is Ovshinsky that white arrow is signified
The M for precipitating in vivo23C6Carbide region.
Can be observed by transmission electron microscope (TEM), in M7C3In carbide and austenite interface, one is formd
Individual continuous Malpighian layer.In Fig. 4, black arrow only indicates the visible M-region under the multiplication factor of Fig. 4, in fact,
Transmission electron microscope display Malpighian layer includes the very thin Malpighian layer of two-layer, including one and M7C3Carbide is neighbouring
Highly brittle high carbon martensite thin layer and the relatively low low-carbon martensite layer of the fragility adjacent to austenite.But, even if in Fig. 4
In visible region, it is also possible to it was observed that some martensitic needles extend to austenite from interface.
In order to minimize crackle, the composition of most of industrial high chromium white cast iron casting body is limited to eutectic mixture.However, one
As think, the rate of wear of high chromium white iron and nascent M7C3Carbide and eutectic M7C3The volume fraction of carbide is directly related,
Therefore, in most cases, hypoeutectic alloy and eutectic alloy have the faster rate of wear than hypereutectic alloy.To hypoeutectic and
The selection of eutectic mixture, can be by reducing M7C3Carbide and austenite boundaries region minimize crackle, due to border horse
The presence of family name's body layer, it has been found that the borderline region is the path that crackle occurs.The industrial alloy of Fig. 2 to Fig. 4 has eutectic to mix
Thing, so, there is provided sample in contain crackle and border martensite.
High chromium white iron can be hypoeutectic, eutectic or hypereutectic state in the present invention, can be used to cast or be heat-treated.Two
Kind hypereutectic mixture can be used the small-sized crucible of cooling at a slow speed to carry out tentative casting.Fig. 5 small-sized cools down at a slow speed crucible to take from
The sample displaing micro picture for casting and being etched through sour iron chloride, the blending constituent of experiment is as shown in Table IV.
Table IVThe hypereutectic body of casting composition of the present invention
| C | Mn | Si | Cr | Ni | Fe/ impurity | |
| Alloy 1 | 4.25 | 9.31 | 2.18 | 27.45 | 4.07 | Balance |
| Alloy 2 | 4.73 | 11.16 | 1.39 | 28.56 | 8.46 | Balance |
These features in Fig. 5 are critically important.Photoetch is mutually the nascent M of hexagonal7C3Carbide bar, and by an austenite light
Ring is surrounded.With the resolution ratio (resolution ratio with Fig. 2 is similar) of Fig. 5, come into being M7C3Carbide or eutectic M7C3Carbide and austenite
Interface on do not appear to dark colour Malpighian layer.Light microscope (high resolution than Fig. 4) has been used in Fig. 6 to be carried out
Careful observation, but still any martensite is not found on the surface.The larger primary carbide of volume shows in micro-structural
Alloy is in hypereutectic state, and as previously described, wear resistance can increase with the increase of the volume fraction of carbide, especially
Primary carbide.
Despite the presence of hole and hypereutectic compound, do not shown with the presence of crackle still in crucible casting.
So, for summary, in the industrial body of casting micro-structural of Fig. 2 to Fig. 4, containing just in separate austenitic matrix
Raw M7C3Carbide, this shows the body of casting for hypereutectic mixture and in as-cast condition.In industrial body of casting micro-structural,
M7C3There is a Malpighian layer between carbide and austenite, because industrial body of casting cooling velocity is relatively slow, this layer of martensite can
It is high-visible in light microscope, present invention, avoiding the generation of interface martensite.
Conversely, tentative mixture cools down at a slow speed the micro-structural of the body of casting and shows the body of casting for hypereutectic composition in the present invention,
The M of the body of casting7C3Carbide and Austenite Interfacial also there is no indication that with the presence of martensite, and exist without crackle.
In the present invention, if composition is observed without transmission electron microscope, with a simple experiment can also judge from
Whether martensite is respectively present in micro-structural in Fig. 2 to Fig. 4 and Fig. 5 and Fig. 6.In each hypereutectic high-chromium white iron, casting
Unique ferromagnetic phase that may be present is exactly martensite in making state, is ferromagnetic from the industrial body of casting in Fig. 2 to Fig. 4 displaing micro pictures
Body, attracts the very capable of magnet, and this shows the inside with the presence of martensite.Composition is constituted in the body of casting and Table IV in Fig. 5 and Fig. 6
Other body of castings can not attract magnet, this shows the inside in the absence of martensite.
Embodiment --- weldering is applied
When being applied for welding deposited or hardening weldering, the present invention can be avoided in M completely7C3Generated on carbide and austenite interface
Malpighian layer.The method for reaching this purpose is similar with above-described casting, be all using as the silicon of martensite promoter and
Reach balance to realize as the manganese of austenite stabilizer and the content of nickel, however, weldering is covered with bigger advantage.Avoid martensite
Generation, while reduce M7C3Interconnection degree in carbide, can Crack prevention generation.On reducing M7C3Carbide
Contiguity this result will be in marginal data below.
We observe it is several carried out in steel matrix hardening weldering it is conformal into hypereutectic high-chromium white iron weldering be coated with cap rock
Industrial sample.Under each case, there is crackle to occur during white iron Surface hardened layer.The shooting figure of Fig. 7 shows typical crackle,
Crack growth to whole hardened surface is explicitly shown out in Fig. 7, it is measurable to 5~10mm eyed structures with centimetre chi.It is most of
In the case of, crackle can radiate the interface that matrix and hardened surface are reached through whole hardened surface thickness.
Every kind of industrial sample uses identical specimen preparation techniques, and sample preparation includes sampling and plasma cut into conjunction
Suitable size, is that grinding and cutting is prepared, and the sample for metallographic detection is cut using abrasive disc and uses water as lubricious
Agent, sample keeps suitable distance with plasma cut area during cutting, and micro- knot will not be made due to heating when can so ensure cutting
Structure changes.Sample section should be obtained along the cutting of welding bead horizontal and vertical direction, and it is wide that size is about 25mm 10mm long, transverse cuts sample
The viewing plane of section be across the direction of continuous pass, the viewing plane of longitudinally cutting sample section then along welding bead direction, these
Sample section is polished using Pyatyi emery paper, most finish is reached 1 μm through diamond paste polishing afterwards, the sample after polishing
Through sour iron chloride (5 grams of FeCl3, 10 milliliters of HCL and 100 milliliter of H2O observed using light microscope after) etching.
Case-hardened representative industrial sample is studied by obtaining and making metallographic along the horizontal and vertical cutting of welding bead in Fig. 7
With.Fig. 8 a and Fig. 8 b are the micro-structural that sample is cut in horizontal and vertical direction, are shown after sour iron chloride etching, and come into being M7C3Carbon
The presence of compound represents that high chromium white iron is hypereutectic composition.The chemical composition of the hardened surface shown in Fig. 7 comes from sample I such as tables
Shown in V, the composition of the hardened surface of other industrial samples comes from sample II and sample III.
Table VHardening fibre surface composition
| Sample | C | Si | Cr | Mn | Fe/ impurity |
| I | 4.9 | 0.94 | 27.3 | 1.2 | Balance |
| II | 5.0 | 1.1 | 25.2 | 1.34 | Balance |
| III | 4.6 | 1.2 | 18.7 | 1.19 | Balance |
The characteristics of industrial sample of observation is common is that have crackle to produce, and all samples all contain in Surface hardened layer whole region
There is the crackle of 5~10mm eyed structures, most of crackle can extend to the interface of matrix and hardened surface, under certain situation,
Crackle can be along further fork and the expansion of matrix and hardened surface interface, and the enlarged meeting of crackle causes hardening on these interfaces
Surface coverage areas separate with matrix surface.
The micro-structural of coverage rate can lift wearing character, and it is critically important for optimization polishing machine.Covering in detection sample
Lid micro-structural is hypereutectic high-chromium white iron micro-structural, and the micro-structural is by the nascent M in austenite eutectic composition7C3Carbide connects
Extension bar and eutectic M7C3Carbide is constituted.But, the micro-structural of detection also includes bad feature, and such as complex rule is mutually connected
The carbide for connecing.
Fig. 9 is the desired microstructure that surface is applied in hardening weldering.Fig. 9 comes from the sample II in Table V, but be not this sample or
The representative of other samples.Micro-structural peracid iron chloride etching in Fig. 9, micro-structural includes M7C3Carbide and austenite
Nascent M in eutectic matrix7C3The hexagonal bar of carbide (white), when the latticed austenite ring of light is around primary carbide
It can be seen that when, primary carbide bar is almost vertical with the shown plane of Fig. 9, therefore it seems almost hexagon.Carbide bar
Profile change with the difference in their directions, so, for stock when primary carbide extends vertically up to the plane of Fig. 9 shootings
Shape, rather than hexagon.
During material melt supercooling, that is to say, that liquid is cooled down before solidification with subnormal setting temperature, no
The normal eutectic phenomena shown in Fig. 9 can be produced, and is taken from the sample III of Table V, the carbides in austenite bar shown in Figure 10
Interconnection fork arrangement.Micro-structural in Figure 10 is the representative of all samples, including shown in Fig. 9 it is under-represented micro-
The sample II of structure.
Eutectic after being etched through sour iron chloride in Figure 10 is still by M7C3Carbide bar (white) and austenite mixed group
Into carbide bar direction is substantially parallel with region shown in Figure 10.The eutectic of this sub-cooled is referred to as the eutectic of complex rule
Body, the diameter of eutectic bar is about 1/5th of primary carbide bar shown in Fig. 9, and has a three fold rotational symmetry knots
Structure, this can cause the triangular appearance of carbide group.Due to the interconnection of these eutectic bars, this micro-structural expands for crackle
There is provided the path of interconnection long.Therefore the micro-structural in Figure 10 is Poor structure, although its Gao Ge before this invention
White iron weldering is very common in applying.
Found after etching sample is carried out into EBSD (EBSD) and X-ray diffraction, all complex rule eutectics
The carbide bar of equilateral triangle is to interconnect in body, wherein, the carbide bar of complex rule is M7C3, its hexagon
Cross section and nascent M7C3The cross section of carbide is identical, although the carbide of complex rule is more preferably, about the five of primary carbide
Times, " particle " of this complex rule structure in terms of millimeter is common.Figure 11 a and Figure 11 b show in more detail in sample II
Situation of the crackle through the micro-structural of this complex rule.
Because the interconnection of carbide bar in eutectic greatly reduces, Fig. 9 shows more preferably eutectic micro-structural,
Same to sample II, this micro-structural contains eutectic M7C3Nascent M in carbide and austenite mixed matrix7C3Bar,
And in the absence of the micro-structural of the complex rule with the carbide being connected with each other.
Carbide Phases connect in other high chromium white iron micro-structurals, and it is molten to facilitate hypereutectic high-chromium white iron to enter row metal
There is embrittlement when deposited, because containing the nascent M of fork in structure7C3Carbide (such as sample III of Figure 12) or fork just
Raw M7C3With the mixture (the sample III of Figure 13) of complex rule structure, increase the silicone content in alloy or improve cooling velocity and hold
Easily generate both structures.
As described above, when silicone content is high, and the cooling velocity being exceedingly fast intrinsic when overcooled weldering can be caused to apply, hold
The easy micro-structural of the primary carbide of generation fork and complicated rule, the growth of these carbide be not be decided by thermograde and
It is overcooled degree.Supercooling more readily occurs in the region for closing on matrix, thus these carbide growths direction and base
Body is parallel rather than vertical with matrix, if the growth of carbide can be by thermograde control, above-mentioned situation is exactly our institutes
Wish to.
This explains the crackle occurred during industrial sample Surface hardened layer.In Fig. 7, crackle is on covering surface in the form of grid
Occur, although these crackles are near matrix surface generation, the crackle for therefore appearing in covering surface can be from matrix always
Covering surface is expanded to, after residual stress effect when this crack pattern is weld seam solidification and the arrangement of carbide bar is produced
Really.Away from matrix, carbide may grow parallel to thermograde, that is, be grown perpendicular to the direction of matrix.
The electron micrograph sector-meeting for examining Figure 14 obtains further explanation.Shown in Figure 14 is sample III, and it is
The electron microscopic picture of high chromium white ferrous metal deposition coating in sample I, II and III, and shown with high-amplification-factor.Although
Figure 14 is the picture of eutectic carbide and austenite, but situation is identical with the primary carbide in austenitic matrix.
Crackle in high chromium white iron coating already described above can typically be sent out along carbide and austenite interface
Raw, this is a thin layer martensite, horse around the thin dark colour region (being shown in Figure 14 less than 0.2 μ m-thick) of carbide particle
Family name's body acupuncture can extend to austenite from these thin layers, and the brittle martensite for around having carbide particle is acted in residual stress
Under, for Crack Extension provides preferable path.During in the absence of Malpighian layer, harder austenite can absorb these remnants should
Power, therefore in M7C3On carbide and austenite interface, crackle would not occur.
It follows that (both containing interconnection in the presence of the primary carbide or complex rule structure of fork
Carbide) or there is martensite on carbide austenite interface can all promote crackle to generate.If these factors can be eliminated,
Weldering can also eliminate crackle when applying.
Two hypoeutectic high chromium white iron are carried out into weldering on low-carbon (LC) steel disk using plasma transferred arc (PTA) to apply, Table VI
Shown is powdered ingredients.
Table VIComposition of the invention
| C | Mn | Si | Cr | Ni | Mo | Fe/ impurity | |
| Alloy 1 | 2.35 | 3.21 | 0.5 | 20.58 | 3.34 | 0.04 | Balance |
| Alloy 2 | 2.25 | 2.86 | 0.47 | 19.51 | 2.97 | 0.04 | Balance |
We have found that constituent structure excellent is applied in this weldering.Figure 15 is the shooting picture that sample section is applied in two-layer weldering, each
Sample section is all that typical weldering is applied.In figure it can be seen that, the deposited surface of weldering is smooth, and with glossy, no slag and no surface are split
Line.In addition, magnet near weldering apply when, be not in signify martensite exist ferromagnetic attraction phenomenon.
Narration (corresponding with Fig. 7 to Figure 14) above with respect to sample I, sample II and sample III is concentrated mainly on nascent M7C3
The adverse effect that Carbide Phases connect.However, as shown in figure 14, in M in those samples7C3Carbide and Austenite Interfacial can
Detect with the presence of martensite, therefore each also show powerful ferromagnetism in sample I, II and III, that is to say, that sample
After this I, sample II and sample III enter row metal deposition, powerful attraction can be produced to magnet.
Figure 16 and Figure 17 are respectively the displaing micro pictures along the horizontal and vertical shooting of welding bead.
Figure 15, Figure 16 and Figure 17 show that weldering is produced without crackle completely in applying.The characteristics of micro-structural is internal tree-shaped crystalline substance
And M7C3And the eutectic of austenite, and in M7C3Carbide and austenite interface do not exist martensite, in addition, M7C3Carbonization
The interconnection degree of thing is also than relatively low.Two kinds of powder cause fabulous mobility and about 10%~25% dilution.Invention
Middle matrix needs pre-heated degree to be also significantly less than prior art, about at 150 DEG C rather than 300.℃
Finally, we welcome to carry out embodiment described above within the scope of the present invention other modifications and correct.
Claims (10)
1. a kind of anti-wear high chromium white iron, with hypoeutectic mixture, eutectic mixture or hypereutectic mixture, its feature exist
In,
Carbon content is 2.5%~4.0% in the hypoeutectic mixture, and chromium content is 18.0%~27%, and nickel content is 4.0%
~8.0%, silicone content is 0.25%~2.75%, niobium or vanadium or both combined content is up to 10%, and 4.0%~
8.0% manganese, also contains ferro element and other alloying elements and impurity in addition；
Carbon content in the eutectic mixture is 3.0%~4.0%, and chromium content is 15.0%~27.0%, and nickel content is
4.0%~8.0%, silicone content is 0.25%~2.75%, and 4.0%~8.0% manganese, in addition also containing ferro element and its
His alloying element and impurity；Or carbon content is 4.25%~4.75%, chromium content is 15.0%~27.0%, and nickel content is
4.0%~8.0%, silicone content is 0.25%~2.75%, and niobium or vanadium or both combined content are up to 10%, and 4.0%
~8.0% manganese, also contains ferro element and other alloying elements and impurity in addition；And
Carbon content in the hypereutectic mixture is 4.0%~5.0%, and chromium content is 20.0%~27.0%, and nickel content is
4.0%~8.0%, silicone content is 0.25%~3.25%, and 4.0%~8.0% manganese, in addition also containing ferro element and its
His alloying element and impurity；Or carbon content is 5.0%~6.0%, chromium content is 20.0%~27.0%, and nickel content is
4.0%~8.0%, silicone content is 0.25%~3.25%, and niobium or vanadium or both combined content are up to 10%, and 4.0%
~8.0% manganese, also contains ferro element and other alloying elements and impurity in addition；
Containing silicon as martensite promoter in wherein described white iron, and manganese and nickel are used as austenite stabilizer, wherein horse
The content of family name's body accelerator and austenite stabilizer is appropriate so that effect balance between the two, such white iron is without Overheating Treatment
In the case of have a kind of micro-structural, the micro-structural is in austenite and M7C3Do not exist martensite on carbide interface.
2. white iron according to claim 1, it is characterised in that the content of the martensite promoter and austenite stabilizer,
And cooldown rate is appropriate so that these become graded effects reaches balance, thus obtained white iron is in the case of without Overheating Treatment
With a kind of micro-structural, M in the micro-structural7C3Carbide has certain interconnection degree, so that not having in the micro-structural
There is the carbide particle of fork.
3. according to the white iron of claim 1 or 2, it is characterised in that the white iron is hypoeutectic mixture, the interface
Including primary austenite and eutectic M7C3Interface and eutectic austenite and eutectic M between carbide7C3Between carbide
Interface.
4., according to the white iron of claim 1 or 2, it is characterised in that the white iron is eutectic mixture, the interface exists
Eutectic austenite and eutectic M7C3Between carbide.
5. according to the white iron of claim 1 or 2, it is characterised in that the white iron is hypereutectic mixture, the interface
Including the M that comes into being7C3Interface and eutectic austenite and eutectic M between carbide and eutectic austenite7C3Between carbide
Interface.
6. a kind of method for producing anti-wear high chromium white cast iron casting body, the white iron body of casting has hypoeutectic mixture, eutectic
Mixture or hypereutectic mixture, it is characterised in that
Carbon content is 2.5%~4.0% in the hypoeutectic mixture, and chromium content is 18.0%~27%, and nickel content is 4.0%
~8.0%, silicone content is 0.25%~2.75%, niobium or vanadium or both combined content is up to 10%, and 4.0%~
8.0% manganese, also contains ferro element and other alloying elements and impurity in addition；
Carbon content in the eutectic mixture is 3.0%~4.0%, and chromium content is 15.0%~27.0%, and nickel content is
4.0%~8.0%, silicone content is 0.25%~2.75%, and 4.0%~8.0% manganese, in addition also containing ferro element and its
His alloying element and impurity；Or carbon content is 4.25%~4.75%, chromium content is 15.0%~27.0%, and nickel content is
4.0%~8.0%, silicone content is 0.25%~2.75%, and niobium or vanadium or both combined content are up to 10%, and 4.0%
~8.0% manganese, also contains ferro element and other alloying elements and impurity in addition；And
Carbon content in the hypereutectic mixture is 4.0%~5.0%, and chromium content is 20.0%~27.0%, and nickel content is
4.0%~8.0%, silicone content is 0.25%~3.25%, and 4.0%~8.0% manganese, in addition also containing ferro element and its
His alloying element and impurity；Or carbon content is 5.0%~6.0%, chromium content is 20.0%~27.0%, and nickel content is
4.0%~8.0%, silicone content is 0.25%~3.25%, and niobium or vanadium or both combined content are up to 10%, and 4.0%
~8.0% manganese, also contains ferro element and other alloying elements and impurity in addition；
Methods described includes：
Casting high chromium white fusant, wherein the melt contains silicon as martensite promoter, and manganese and nickel are used as Ovshinsky
Body stabilizer；
The melt is cooled down, the obtained body of casting has a kind of micro-structural, and the micro-structural includes in the case of without Overheating Treatment
Austenite and M7C3The content and cooldown rate of carbide, martensite promoter described in melt and austenite stabilizer are appropriate
So that these become graded effect reaches balance, the thus obtained white iron body of casting has a kind of micro- knot in the case of without Overheating Treatment
Structure, the micro-structural is in austenite and M7C3Do not exist martensite on carbide interface.
7. method according to claim 6, it is characterised in that martensite promoter and the austenite stabilization in the melt
The content and cooldown rate of agent are appropriate so that these become graded effects reaches balance, the thus obtained white iron body of casting without
There is a kind of micro-structural, M in the micro-structural in the case of Overheating Treatment7C3Carbide has certain interconnection degree, so that
There is no the carbide particle of fork in the micro-structural.
8. the method according to claim 6 or 7, it is characterised in that the high chromium white cast iron casting body is hypoeutectic mixture,
The interface includes primary austenite and eutectic M7C3Interface and eutectic austenite and eutectic M between carbide7C3
Interface between carbide.
9. the method according to claim 6 or 7, it is characterised in that the high chromium white cast iron casting body is eutectic mixture, institute
Interface is stated in eutectic austenite and eutectic M7C3Between carbide.
10. according to the method for claim 6 or 7, it is characterised in that the high chromium white cast iron casting body is hypereutectic mixture, institute
Stating interface includes nascent M7C3Interface and eutectic austenite and eutectic M between carbide and eutectic austenite7C3Carbon
Interface between compound.
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| CN201510382089.7A CN105132791B (en) | 2004-10-27 | 2004-10-27 | A kind of abrasion-proof alloy of improvement |
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| CN201510382089.7A CN105132791B (en) | 2004-10-27 | 2004-10-27 | A kind of abrasion-proof alloy of improvement |
| CNA2004800447202A CN101133175A (en) | 2004-10-27 | 2004-10-27 | Improved abrasion-proof alloy |
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| CN108085583A (en) * | 2017-12-19 | 2018-05-29 | 西南科技大学 | A kind of wear member, content and high manganses and chromium content white cast-iron and preparation method thereof |
| CN110551938A (en) * | 2019-09-27 | 2019-12-10 | 中国科学院金属研究所 | Alloy powder for melting wear-resistant layer of agricultural machine part |
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| SU1344807A1 (en) * | 1986-01-06 | 1987-10-15 | Липецкий Филиал Всесоюзного Проектно-Технологического Института Литейного Производства | Wear-resistant cast iron |
| SU1425245A1 (en) * | 1986-12-29 | 1988-09-23 | Предприятие П/Я Х-5886 | Wear-resistant cast iron |
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