CN101133175A - Improved abrasion-proof alloy - Google Patents

Abstract

A wear resistant, high chromium white iron, in an unheat-treated condition has a microstructure substantially comprising austenite and M7C3 carbides. The white iron contains at least one martensite promoter and at least one austenite stabiliser which are present at respective levels to achieve a balance between their effects whereby the white iron is substantially crack-free. The white iron may be as-cast or comprise well deposited hardfacing.

Description

A kind of abrasion-proof alloy of improvement

Technical field

The invention belongs to the technical field of abrasion-proof alloy, particularly a kind of parts surface that is suitable for hardens, and also can carry out finished product direct pouring, the white pig iron of the improved anti-wear high-chromium amount of its fracture toughness property.

Background technology

Contain chromium white iron, high chromium white iron particularly is owing to contain hard M ₇C ₃Carbide has very strong anti-wear property, and M is Fe, Cr or Cr, Fe here, but also may contain a small amount of other elements such as Mn or Ni according to composition, and this anti-wear high chromium white iron may be hypoeutectic, eutectic or hypereutectic state.

The carbon content of hypoeutectic high chromium white iron is up to 3.0%.Contain in its microstructure and be present in M ₇C ₃The tree-shaped crystalline substance of primary austenite in carbide and the austenite eutectic mixture matrix.The phosphorus content of eutectic white pig iron is 3.0%-4.0%, and its microstructure is M ₇C ₃Carbide and austenitic eutectic mixture.The phosphorus content of hypereutectic white iron is 3.5%-5.0%, and its microstructure contains and is present in M ₇C ₃Nascent M in carbide and the austenite eutectic mixture matrix ₇C ₃Carbide.In every kind of situation, M just ₇C ₃Carbide as eutectic carbide or primary carbide, makes this alloy have anti-wear characteristic.Hypereutectic white iron is compared with hypoeutectic white iron and is contained how hard antiwear M ₇C ₃Therefore carbide often becomes the first-selected alloy that the weldering of hardening is applied.Yet hypereutectic white iron generally is unsuitable for casting, and the crackle that produces when reason is cooling causes stress to produce.

In general, if improve the anti-wear characteristic of hypereutectic high-chromium white pig iron, its fracture toughness property will decrease.High chromium white iron is widely used in anti-wear property requirement height and fracture toughness property lower mining and the processing minerals of requirement relatively.Yet other application requiring material has higher fracture toughness property, and this just means that hypereutectic white iron can not be applied in these occasions, and for addressing this problem, people have done different trials.

The background technology of Australian Patent AU-A-28865/84 relates generally to the high chromium white iron of hypoeutectic and hypereutectic mixture, it has described the repeatedly test of failure, attempt to make the hypereutectic white iron alloy that has anti-wear property and fracture toughness property concurrently that is suitable for casting, AU-A-28865/84 has also described test several times simultaneously, attempts to make the hypoeutectic synthetics that has anti-wear property and fracture toughness property concurrently and is suitable for hardening the deposited alloy of weldering.Yet, AU-A-28865/84 has in fact mainly solved the crack problem of cast iron mixture by casting hybrid shaping, just a kind of particular alloy and matrix are carried out metallurgical binding, when alloy cools off, eliminate the possibility that crackle occurs then, form the cast iron mixture at last.Really, AU-A-28865/84 attempts by guaranteeing that the main component in the cast iron mixture is that sectional dimension is not more than 75 microns M ₇C ₃Carbide solves phosphorus content greater than low fracture toughness and the crack problem of 4.0% hypereutectic cast iron, advises that also number of mechanisms does this trial.Like this, the AU-A-28865/84 purpose is by forming main component M in blending constituent and the restriction alloy ₇C ₃The size of carbide solves problem.

United States Patent (USP) 5,803, the microstructure of 152 attempt refining hypereutectic white irons, the microstructure of especially thick hypereutectic white iron makes the nucleation amount of main component carbide reach maximum, increases the fracture toughness property and the anti-wear property of material with this.Refining is exactly to add a kind of special metal in the toppling process that the molten metal fluid is cast, and this metal will therefrom absorb heat, and overcooling is carried out in the deposite metal, thereby makes it enter the first state that solidifies between liquid state and the solid state temperature.

The fracture toughness property that improved the surface hardening alloy with former trial is the same, United States Patent (USP) 6,375,895 point out, although made preventive measures in advance, much formerly in the technology, case-hardened high chromium white iron always has thick crackle net more or less to occur under welded condition.United States Patent (USP) 6,375,895 propose, and the remollescent austenitic matrix (can cause metal shrinkage crack to occur when molten state is cooled off after about 300BHN～600BHN) hardness of middle primary carbide (about 1700 Brinell hardness (BHN)) acquires a certain degree.United States Patent (USP) 6,375,895 terms of settlement is to adopt a kind of special alloy mixture, before surface hardening, preheat the matrix of mixture, cool off whole mixture then, this can guarantee to have all the time in the microstructure martensite to exist and whole alloy rigidity (the about 455BHN～512BHN) that is consistent.

The purpose of this invention is to provide a kind of anti-wear high chromium white iron that the flawless Wimet uses that is suitable for casting and can be used as.This high chromium white iron does not need to generate blending constituent and does not need complicated foundry engieering yet when casting, simultaneously, when carrying out the surface sclerosis, do not need to carry out the expensive processing that preheats yet.

Introduce before the present invention, at first the formerly description of technology only is background technology explanation more than the statement, and these formerly references of technology are not represented that these patent-related document disclose and enter the public information scope in that Australia or other are local.

Summary of the invention

The inventor illustrates the low reason of anti-wear high chromium white iron fracture toughness property first.The inventor has been found that M ₇C ₃There are a thin layer martensite in carbide and austenite interface, and this thin layer martensite causes or caused at least crackle.This all is suitable for following situation: M ₇C ₃Carbide is primary carbide, and austenite is in eutectic matrix; Or M ₇C ₃Carbide is eutectic carbide, and austenite is eutectic austenite; Or M ₇C ₃Carbide is eutectic carbide, and austenite is primary austenite.Like this, the hypoeutectic that this discovery can be applicable to cast, eutectic and hypereutectic high-chromium white iron, this discovery also can be applicable to eutectic and hypereutectic alloy and many (as not being whole) hypoeutectic alloy of welding.

In addition, the inventor determines that the common thickness of this martensite thin layer may for one to several micron, also may only have several nanometers.This thin layer may not be also may variable thickness to cause fully continuously around carbide, and this thin layer also can only just can be observed under the instruments such as electron microscope certainly.

This discovery is pointed out, in high chromium white iron, because M ₇C ₃Carbide and austenite have caused the martensitic formation of thin layer in abutting connection with the minimizing of chromium and the carbon at position.This discovery is also pointed out, contains silicon in the composition and can cause M ₇C ₃Generate martensite between the austenite of carbide and vicinity.

This discovery is pointed out, material contracts when solidifying postcooling owing to deposited metal, and the deposited body of the weldering that the sclerosis weldering generates when applying is inner can to produce tensile residual stresses.Also point out in the discovery, with M ₇C ₃Contiguous this layer martensite thin, hard and fragility of carbide can discharge these tensile stress by crackle, if there is not the thin martensite of this layer, softer austenite then can absorb these tensile residual stresses and produce distortion, and this has hindered the generation of crackle and has made the micro-crack extension degree reduce to minimum.

The inventor also finds, at M ₇C ₃The martensite that carbide and austenite interface exist is not the sole cause that causes crackle to produce during casting and sclerosis weldering are applied, one more chief reason (will describe in detail in the back) be the M in the material ₇C ₃The Carbide Phases degree that connects is very high, adds some alloys and can improve M ₇C ₃The degree that interconnects of carbide.This alloy additive effect is very big, and interpolation wherein a kind of alloy just can make material solidify front supercooling, and this can be applicable to casting and weldering is applied, as the M of height connection degree ₇C ₃Carbide be positioned at M ₇C ₃When the martensite between carbide and the austenite existed simultaneously, the generation of crackle and expansion were just inevitable.Blue M ₇C ₃The height connection situation of carbide occurs in the alloy, and these alloys are difficult for when martensite appears in adjacent surface, although the root of crackle can avoid, generally speaking the crackle in the material generate and expansion still inevitable.

The inventor points out that in most cases, still weldering is deposited no matter to be applied to casting, and it all is identical solving the generation of crackle in the high chromium white iron and the method for expansion.

The invention provides a kind of anti-wear high chromium white iron, described white iron without Overheating Treatment has a kind of micro-structural, contains austenite and M in the micro-structural ₇C ₃Carbide contains at least a martensite promoter and at least a austenite stabilizer in the described white iron, and described martensite promoter and austenite stabilizer content are suitable, and effect reaches balance, makes white iron not have crackle.Under most of situation, this white pig iron is flawless and have better fracture toughness property not only.

A kind of form is arranged, and white iron is in as-cast condition, the content of martensite promoter and austenite stabilizer suitably and effect reach and cause balance so that M in the white iron ₇C ₃There is not martensite on the interface between carbide and austenite.

Another kind of form, white iron contains the hardened surface that the matrix through welding after applying provides, and this hardened surface flawless exists.Martensite promoter and austenite stabilizer effect reach and cause balance, make the M in the micro-structural ₇C ₃In the carbide, the degree that interconnects between its carbide particulate reaches a relatively low level, like this, does not have branch's carbonized particles in the micro-structural, and the content of described martensite promoter and austenite stabilizer suitably reaches and causes balance, makes white iron at austenite and M ₇C ₃There is not martensite on the interface of carbide fully.

The invention provides a kind of M ₇C ₃Do not have martensitic anti-wear high chromium white ferroalloy on carbide and the Austenite Interfacial, no matter this alloy forms hardened surface through casting or through welding to apply, and does not all have crackle fully.Yet, should be clear and definite be not have martensite can not get rid of the possibility that austenite inside has martensite to exist beyond the interface on the above-mentioned interface.This characteristic feature of an invention is at M ₇C ₃Can not form the martensite thin layer on carbide and the austenite interface, rather than get rid of the possibility that martensite exists in other zones yet.In fact, in some compositions, beyond the interface some martensitic existence must be arranged.

Another kind of form the invention provides a kind of anti-wear high chromium white iron, and wherein at least a martensite promoter and at least a austenite stabilizer have fully reached the effect balance, make M ₇C ₃Do not have martensite on carbide and the Austenite Interfacial, so white iron can not crack through casting or through the deposited hardened surface that forms of weldering.

One of alloying element silicon is exactly a kind of martensite promotor, and it can promote martensitic generation, and this combination gold element also comprises boron.In high chromium white iron of the present invention, silicon is most important martensite promotor, can reach required balance with at least a austenite stabilizer.Yet boron also can be used as the use of a kind of martensite promotor, and content can reach 1% or even up to 2% during use.Adding boron can influence the activity of silicon, and boron also can be used as single martensite promotor.In general, boron also can be used as martensite promotor, but the control of implementing among the present invention mainly is at silicon and at least a austenite stabilizer as martensite promotor.

One of alloying element should be as at least a austenite stabilizer, and its effect is the generation of promotion and stable austenite.This combination gold element comprises manganese, nickel, copper and molybdenum, and these elements can use separately also use capable of being combined, and in four kinds of elements, the effect in the present invention of manganese and nickel is especially remarkable.Though a small amount of at least a other austenite stabilizers also are provided in the invention, and control of the invention process mainly is at manganese and/or nickel as austenite stabilizer.Equally, should be clear and definite be also to use other austenite stabilizers to replace manganese and/or nickel.

In the better scheme of the present invention, an amount of austenite stabilizer (such as manganese or nickel) and the martensite promoter (such as silicon or boron) that different alloying elements consists of reaches " fully effect balance ", has suppressed M ₇C ₃The generation of carbide and Austenite Interfacial Markov body thin layer.This " fully balance " that these an amount of alloying elements that exist in the high chromium white iron reach makes material in casting or hardens to weld when applying and can not generate crackle.

Further these alloying elements of research, the someone advises a martensite promoter (such as silicon) as some high chromium white iron additives, to improve that its sclerosis weldering is applied or melt fluidity during casting.But, the inventor finds, the existence of martensite promoter (such as silicon) can produce the result that quite unexpected accumulative total worsens, the existence meeting of martensite promoter produces negative impact and causes martensitic generation austenite stabilizer, therefore, martensite promoter does not just promote martensitic generation, and more can promote at austenite and M ₇C ₃The generation of carbide interface Markov body, Here it is martensite promoter (such as silicon) and austenite stabilizer will reach the reason of " fully balance ".

Although silicon can promote martensite to generate, the content of silicon should increase or remain on certain level, because the use of austenite stabilizer can be offset the effect of martensite promoter.In other words, although the existence of silicon is having good result aspect the melt fluidity improving, austenite stabilizer still must reach sufficient level, and this can prove by the general Metallographic Techniques of usefulness.Finding have martensite to generate in the high chromium white iron that is suppressed, that show in the microphoto that utilizes Metallographic Techniques to obtain mainly is the primary austenite of hypoeutectic iron and the nascent M of eutectic matrix and hyper-eutectic irons ₇C ₃Carbide and eutectic matrix, the conclusion that draws are to contain austenite and M in the eutectic thing ₇C ₃Carbide, and do not have martensite.For the tree-shaped crystalline substance of hypoeutectic white iron, main tree-shaped crystalline substance all formed by austenite or austenite in some zone also contain martensite, under latter event, if martensite is included in the austenite, these contain martensitic zone is acceptable.Which kind of situation no matter, the result that microphoto shows is identical with expectation, and the crackle that occurs in the photo also satisfactory and available residual stress is explained, need not further observation.

As aforementioned, although we find to exist austenite stabilizer, silicon can promote what martensite generated, at M ₇C ₃When generating martensite on carbide and the Austenite Interfacial, this facilitation is harmful to, and these interfaces may be the carbide of eutectic phase and the combination of austenite or primary austenite and eutectic carbide or primary carbide and eutectic austenite or these situations.

Cast or weld flowability when applying in order to increase material, need the silicone content of certain level in the material.Yet, add silicon not just in order to reach this purpose, add the negative effect that a kind of competent austenite stabilizer neither be only produces during as martensite promotor for offset silicon, a factor is to add austenite stabilizer can increase cost, yet, prior, silicon can produce complicated influence to the microstructure of material.We have found that according to the difference of silicone content, M can be strengthened or reduce to silicon ₇C ₃The degree that interconnects of carbide, the sub-hypereutectic white iron of this major embodiment, but also be applicable to hypoeutectic white iron.

Be entitled as " high chromium white iron " part in 15 volume " castings " the 9th edition 681 pages of ASM handbook and point out that " characteristics are hard relatively discontinuous M to high chromium white iron ₇C ₃Eutectic carbide ".Large-scale nascent M is arranged in the hypereutectic white iron ₇C ₃The hexagonal bar of carbide, and these hexagonal bars are discontinuous.Yet, point out that here silicon can affect the interconnective degree of carbide of eutectic carbide inside and primary carbide inside, increases M ₇C ₃The degree that interconnects of carbide can increase the whole fragility of material, promotes crackle to generate and expansion, on the contrary, reduces M ₇C ₃The degree that interconnects of carbide helps hard austenite to limit mutually generation and the expansion of crackle.

Supercooling phenomenon when silicon can increase the front molten state of material solidification, like this, silicon has increased eutectic M ₇C ₃The degree that interconnects of carbide, and for hypereutectic micro-structural, silicon has increased nascent M ₇C ₃The degree that interconnects of carbide.Simultaneously, the also therefore increase of whole fragility when applying is cast or welded to material.Yet if the content of silicon can be controlled, supercooling just can not take place.Research finds that silicon also can reduce nascent M ₇C ₃Carbide and eutectic M ₇C ₃The degree that interconnects of carbide can improve the fracture toughness of material, anti-wear property and thermal-shock resistance like this.Can reduce eutectic M in the hypoeutectic mixture when silicone content is higher ₇C ₃The degree that interconnects of carbide, the eutectic structure that interconnects so the higher complicated rule of degree can not form in eutectic alloy.

Research is found, should consider another factor when determining silicone content, especially when casting, at present, adopts slower cooling velocity during casting high chromium white iron.683 pages " knockout " part has following narration in the above-mentioned ASM handbook: " but metal cool to room temperature Crack prevention under molten state is generated, especially when the final stage martensite of cooling generates."; this part is further pointed out; carry out heavy mail when casting and should force the measure of taking this pre-Anti-cracking to generate; the reason that frequently produces high residual stress and crackle be foundry goods when separating with mould temperature too high; in other words; the generation reason of crackle is relevant with cooling velocity, slower cooling velocity can reduce generation and the expansion of crackle.

We find, because at least a martensite promotor (as silicon) and at least a austenite stabilizer have reached the effect balance, the increase silicone content can improve speed of cooling and can not crack, and this is very favourable aspect cycle shortening Foundry Production certainly.Yet this discovery also is applicable to the just higher welding of original cooling velocity, because the silicon of high level can reduce the probability that crackle generates by discharging residual stress, and needn't consider that silicone content and cooling velocity are to M ₇C ₃The connect combined effect of degree of Carbide Phases.

Consider above factor, the silicone content in the high chromium white iron of the present invention should be 0.25%～3.5%, yet silicone content is better between 0.5%～3.25% the time.In some forms (by the microstructure decision), silicone content should not be higher than 2.75%, and the back chapters and sections have relevant explanation.In a way, the effect of boron is more effective than silicon, and as previously discussed, the content of boron only requires the highest about 1% or about 2%.

All parameters unless stated otherwise, all are weight percentage.Be applied to sclerosis and weld when applying, this ratio can be diluted by parent metal, is 10%～40% such as allowed band.

In the scheme of first-selection of the present invention, contain austenite stabilizer manganese and nickel in the alloy, content is 4.0%～12%.As in order to prevent that austenite is converted into martensite, its content should be 4.0%～8.0%.Yet, should be clear and definite be, needn't contain simultaneously two kinds of elements in the alloy, as long as because there is a kind of element, and content just can meet the demands in above-mentioned scope.Equally, although in some cases, manganese and/or the nickel content in some alloys can be up to about 12%, and best scope should be 4.0%～8.0%.

When with copper during as austenite stabilizer, its consumption is identical with above-described manganese and/or nickel.Yet the used in amounts of molybdenum increases, because a part of molybdenum need be used for the Formed compound, and this part molybdenum can not use as austenite stabilizer.Like this, should consider to use a kind of substitute of molybdenum as the alloy addition that similar austenite stabilization is arranged.Yet we still recommend copper and these two kinds of elements of molybdenum, but when using, its content will be in reduced levels, and uses in conjunction with manganese and/or nickel.Consider the cost problem, this method is particularly like this for molybdenum.

Here recommend, two or more austenite stabilizer can be used in combination, and the total content of austenite stabilizer should be no more than 20%, had better not surpass 16%.

Reach the balance of requirement of the present invention, must control some variablees, these variablees comprise silicone content, manganese content and nickel content.If manganese and nickel can exchange, two content can be taken a variable as, yet they are as some slight difference of effect of austenite stabilizer, therefore as variable is better separately.The 4th variable is cooling velocity, and as a variable, cooling velocity is relative with the relation of casting larger, because in the situation that weldering is applied, the scope of cooling velocity will be restricted.

Present case shows that we can rule of thumb set up the relation of above-described four variablees.Yet, the known today or empirical relationship that used, as Andrew (Andrew) relation of decision martensite start temperature Ms, all with to reach balance of the presently claimed invention irrelevant, therefore, the form that concerns between four variablees is indefinite.Final result is, high chromium white iron for given carbon and chromium content, must carry out tentative experiment casting and tentative experiment weldering applies, could determine the balance that silicon and manganese and/or nickel should reach like this, the speed of cooling when these tests are implemented should be relevant with the production operation of whole white pig iron composition.Equally, at least in these trials, silicone content should be determined to cause sub-cooled in advance, and like this, the test number (TN) that reaches required balance by the content of regulating manganese and/or nickel will reduce.

In the preliminary test, in the examination body that we can apply a magnet near casting or weldering, determine whether the balance that reaches required with this, if ferromagnetism (whether be used to indicate martensite herein exists) is not obvious, this balance may reach basically.But, detect to determine M with metallographic ₇C ₃Whether carbide and Austenite Interfacial exist martensite then more suitable.

In the high chromium white iron of the present invention, chromium content generally is recommended as 8%～50%, and optimum is 10%～30%.Carbon content is generally 1.0%～6.0%.Yet the content of carbon has some eclipsed subranges, and this is decided by that white pig iron is hypoeutectic, eutectic or hypereutectic state.Carbide is mainly M ₇C ₃Also may there be the relatively low M of a small amount of hardness in form in zones such as primary austenites ₂₃C ₆Carbide.

Carbon content is generally 1.0%～3.0% in the hypoeutectic chromium white pig iron, and carbon content is generally 3.0%～4.0% in the eutectic chromium white pig iron, and carbon content is generally 3.5%～5.0% in the hypereutectic chromium white pig iron.If these scopes can change then be better, whether there are other alloying elements in this determinant material.For example, the total content of niobium and/or vanadium is up at about 10% o'clock (add these two kinds of elements and can generate niobium carbide and vanadium carbide, so that improve anti-wear property) in the material, and the content of the carbon in hypoeutectic, eutectic and the 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 the variation, and this is decided by the difference of contained alloying element.The variation of clear and definite these scopes takes place and how to take place in personnel under what conditions that be proficient in this technology, and this has done relevant explanation in Fig. 1.

Description of drawings

For conveniently understanding the present invention, can be with reference to the accompanying drawings:

Fig. 1 is the chromium white pig iron liquidus line sciagraph of present widespread usage;

Fig. 2 is according to current test form, the displaing micro picture of sample drawn from the hypereutectic body of casting;

Fig. 3 is the displaing micro picture of Fig. 2 subregion, and it is big that magnification becomes;

Fig. 4 is the displaing micro picture of Fig. 2 subregion, and magnification is bigger;

Fig. 5 is the displaing micro picture of the present invention's sample drawn from the hypereutectic body of casting of chromium white pig iron;

Fig. 6 is same sample displaing micro picture among Fig. 5, and it is big that multiplication factor becomes;

Fig. 7 is the crackle shooting figure that the surface is applied in typical prior art sclerosis weldering among the sample I;

Fig. 8 (a) and (b) be the displaing micro picture of sample shown in Figure 7;

Fig. 9 has shown ideal but unrepresentative microstructure for the displaing micro picture of the sample II of use prior art hardened surface;

Figure 10 has shown typical but bad microstructure for the displaing micro picture of the sample III of use prior art hardened surface;

Figure 11 (a) and 11 (b) displaing micro picture for having amplified separately shows that crackle spreads all over the bad microstructure of Fig. 9 sample II;

Figure 12 and Figure 13 are for showing the displaing micro picture of the bad microstructure of Figure 10 sample III respectively;

Figure 14 is the electron microscopic picture of Figure 10 sample III, has shown the bad microstructure features of typical case;

Figure 15 is taking pictures that the typical high chromium white iron weldering of the present invention is applied;

Figure 16 is the displaing micro picture along the welding bead longitudinal cross-section shown in Figure 15;

Figure 17 is the displaing micro picture along the welding bead lateral cross section shown in Figure 15.

Embodiment

Fig. 1 is rich in the liquidus line sciagraph of the Fe-Cr-C of one jiao of Fe for high chromium white iron metastable state C-Cr-Fe liquid phase surface.Carbon content is up to 6% in this three metamember, and chromium content is up to 40%, also contains a small amount of manganese and silicon simultaneously.

What the liquidus line sciagraph among Fig. 1 showed is the relation of microstructure and carbon chromium content.Indicate the region representation hypoeutectic composition of γ, the composition that some A, B, C, D and E are ordered in the general range is called group I.

Composition A and B are in the hypoeutectic zone, and close boundary line.The eutectic micro-structural is present in from U ₁To U ₂Straight line on, near the composition of B along U ₁To U ₂Straight line to the some C.Hypereutectic composition is indicating M ₇C ₃The zone in, comprise components D and E.

Any have the austenite of promotion all should avoid to the methods for cooling of martensite transformation function, concerning some compositions, preferably adopts a methods for cooling that can not promote that martensite generates.Yet, as previously discussed, can reach higher speed of cooling when silicone content is higher.

Embodiment describes in detail

Illustrative blanket embodiment for casting or weld the high chromium white ferrous components that applies of the present invention represents with Table I and Table II.Table I comprises the composition that some A, B, C, D and the E shown in Fig. 1 represents for group I composition.Table II is analogous components (concrete reason above describe in detail), because of comprising niobium and/or vanadium is different.

Table I-group I composition range

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
							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 range

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
							Hypereutectic	5.0～6.0	20.0～27.0	10.0	4.0～8.0	4.0～8.0	0.25～3.25

Attention:

1. in the scope in Table I and Table II, the balance of composition is iron and incidental impurities, yet, can as above-mentioned, add alloying element.

2. in the scope of Table II, the content of niobium and vanadium all can be up to 10%, and preferably total content is 10%.Equally, owing to increase niobium and/or vanadium, must increase the carbon content that it is as shown in the table, to produce carbide.

Embodiment---casting

From being used for industrial high chromium white cast iron casting body, cut one section microstructure features of analyzing this material as sample.This section high chromium white iron can use the cutting of water spray grinding and cutting method to obtain, use a thin silicon carbide rotating disk (circular disc) to cut out sample from this section high chromium white iron, use competent water to cool off during cutting as cooling fluid, use Olympus (Olympus) reflected light microscope of 500 times or above magnification to detect this sample, this sample is detected under non-etching and etching state, and etching reagent is sour iron chloride (5 gram FeCl ₃, 10 milliliters of HCL and 100 milliliters of H ₂O).

Fig. 2 is that industrial body of casting sample is through polishing and the displaing micro picture after sour iron chloride etching.Zone among Fig. 2 is the crosspoint of the lower crackle in surface and face crack, and these large-scale crackles may produce when the body of casting solidifies rear cooling.The high-resolution displaing micro picture of the same area that the left side, point of crossing is taken between crackle as shown in Figure 3.

The microstructure of Fig. 2 and Fig. 3 represents that the industrial body of casting is in the casting state.The industrial body of casting chromium white pig iron that Fig. 2 and Fig. 3 represent is hypereutectic structure, as shown in Table III.

Table III industry 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, can see separately only having nascent M in the micro-structural under the multiplication factor ₇C ₃Carbide and austenite.Although the white iron constituent class seemingly, the micro-structural here is obviously different from common high chromium white iron, among Fig. 2 and Fig. 3, does not have well-regulated M in the austenite ₇C ₃Eutectic carbide, for the eutectic thing of rule, growing up of eutectic phase can promote the generation of second-phase.This different reason occurs and believe the inoculation that uses when the manufacture body of casting, the effect of inovulant then is to make M ₇C ₃Assemble when carbide solidifies, the strength that the driving carbide is grown up enough makes the carbide in the austenite independently solidify, thereby generates divorced eutectic.

Micro-structural among Fig. 2 and Fig. 3 contains the nascent M in the separated eutectic micro-structural ₇C ₃Carbide (white) has been avoided with interconnective, the complicated regular texture of carbide bar, and this produces for Crack prevention is favourable, because the crack path that high chromium white iron casting or weldering produce when applying is along M ₇C ₃Carbide and austenite interface, the eutectic carbide structure of interconnective complex rule provides long continuous path for crack growth, therefore, must eliminate this structure.Yet although the body of casting microstructure among Fig. 2 and Fig. 3 has reached this purpose, crackle still can take place, and reason can be learnt from Fig. 4.

Fig. 4 of high-amplification-factor takes the top in crackle point of crossing in Fig. 2, vertical crack right-hand.Among Fig. 4, light color is nascent M mutually ₇C ₃Carbide, accounting for leading dark matrix is the separated eutectic austenite.Yet, at austenite and M ₇C ₃There is one deck martensite in austenite boundaries zone in the carbide interface, indicates with black arrow.Equally, the white arrow indication is sedimentary M in the austenite ₂₃C ₆The carbide zone.

(TEM) can be observed by transmission electron microscope, at M ₇C ₃In carbide and the austenite interface, formed a continuous Malpighian layer.Among Fig. 4, black arrow is only indicated visible M-region under the multiplication factor of Fig. 4, and in fact, transmission electron microscope shows that Malpighian layer comprises two-layer very thin Malpighian layer, comprising one and M ₇C ₃The high carbon martensite thin layer that is highly brittle and the low-carbon martensite layer that the austenitic fragility of vicinity is lower that carbide is contiguous.But, even in the visible zone of Fig. 4, also can observe some martensitic needles and 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.Yet, it is generally acknowledged the rate of wear of high chromium white iron and nascent M ₇C ₃Carbide and eutectic M ₇C ₃The volume fraction of carbide is directly related, and therefore, in most cases, hypoeutectic alloy and eutectic alloy have the faster rate of wear than hypereutectic alloy.To the selection of hypoeutectic and eutectic mixture, can be by reducing M ₇C ₃Carbide and austenite boundaries zone minimize crackle, because the existence of border Malpighian layer, we find that this borderline region is the path that crackle takes place.Fig. 2 has eutectic mixture to the industrial alloy of Fig. 4, so, crackle and border martensite are provided in the sample that provides.

High chromium white iron can be hypoeutectic, eutectic or hypereutectic state among the present invention, can be used for casting or heat treatment.Two kinds of hypereutectic mixtures can use the small-sized crucible that cools off at a slow speed to carry out tentative casting.Fig. 5 small-sizedly cools off at a slow speed crucible casting and through the etched sample displaing micro picture of sour iron chloride, the blending constituent of test as shown in Table IV for taking from.

The hypereutectic body of casting composition of Table IV 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 among Fig. 5 are very important.Photoetch is the nascent M of hexagonal mutually ₇C ₃The carbide bar, and by an austenite ring of light encirclement.With the resolution ratio (similar with the resolution ratio of Fig. 2) of Fig. 5, nascent M ₇C ₃Carbide or eutectic M ₇C ₃As if there is not the dark colour Malpighian layer on carbide and the austenitic interface.Use light microscope (than the resolution ratio height of Fig. 4) to carry out careful observation among Fig. 6, but still do not found any martensite at this interface.The primary carbide that volume is bigger in the microstructure shows that alloy is in hypereutectic state, and as previously described, anti-wear property can increase with the increase of the volume fraction of carbide, especially primary carbide.

Although have hole and hypereutectic compound, still do not demonstrated crackle in the crucible casting and existed.

Like this, summarize, Fig. 2 contains nascent M in the austenitic matrix that separates in the industrial body of casting micro-structural of Fig. 4 ₇C ₃Carbide, this shows that this body of casting is hypereutectic mixture and is in as-cast condition.In the industrial body of casting micro-structural, at M ₇C ₃A Malpighian layer is arranged between carbide and the austenite, because industrial body of casting cooling velocity is relatively slow, this layer martensite can be high-visible in light microscope, and the present invention has avoided the martensitic generation in interface.

On the contrary, the micro-structural that tentative mixture cools off at a slow speed the body of casting among the present invention shows that this body of casting is hypereutectic composition, the M of the body of casting ₇C ₃Carbide and Austenite Interfacial there is no indication that also martensite exists, and do not have crackle to exist.

Among the present invention, if composition is observed without transmission electron microscope, also can judge whether there is respectively martensite from Fig. 2 to Fig. 4 and in the micro-structural among Fig. 5 and Fig. 6 with a simple experiment.In each hypereutectic high-chromium white iron, may exist in the as-cast condition unique ferromagnetic be exactly martensite mutually, the industrial body of casting from Fig. 2 to Fig. 4 displaing micro picture is ferromagnet, attracts the very capable of magnet, this shows that the inside has martensite to exist.Other body of castings that composition constitutes in the body of casting among Fig. 5 and Fig. 6 and the Table IV can not attract magnet, and this shows that there is not martensite in the inside.

Embodiment---weldering is applied

Be used for welding applying or hardening and weld when applying, the present invention can avoid at M fully ₇C ₃Generate Malpighian layer on carbide and the austenite interface.Reaching the method for this purpose and above-described foundry seemingly, all be with as the silicon of martensite promotor with reach balance as the content of the manganese of austenite stabilizer and nickel and realize, yet weldering is covered with bigger advantage.Avoid martensitic generation, reduce simultaneously M ₇C ₃The degree that interconnects in the carbide, but Crack prevention generates.About reducing M ₇C ₃This result of the contiguity of carbide is marginal data in the back.

We observe several the sclerosis in steel matrix and weld the deposited tectal industrial sample of hypereutectic high-chromium white iron weldering of applying formation.In every kind of situation, there is crackle to occur during the sclerosis of white iron surface.The shooting figure of Fig. 7 has shown typical crackle, clearly demonstrates crack growth among Fig. 7 to whole hardened surface, can measure 5～10mm eyed structure with centimetre chi.In most of situation, crackle can radiate and pass the interface that whole hardened surface thickness arrives matrix and hardened surface.

Every kind of industrial sample all adopts identical sample technology of preparing, the sample preparation comprises sampling and becomes suitable dimension with plasma cutting, for grinding and cutting is prepared, the sample that is used for the metallographic detection uses abrasive disc cutting and water as slipping agent, sample and plasma cutting district keep suitable distance during cutting, can not change owing to heating makes microstructure in the time of can guaranteeing to cut like this.The sample section should obtain along the horizontal and vertical direction cutting of welding bead, it is wide that size is about the long 10mm of 25mm, the viewing plane of transverse cuts sample section is to cross the direction of continuous pass, vertically the viewing plane of cutting sample section is then along the welding bead direction, these sample sections use the Pyatyi emery paper to polish, make fineness reach 1 μ m finally by the diamond paste polishing, the sample after the polishing is through sour iron chloride (5 gram FeCl ₃, 10 milliliters of HCL and 100 milliliters of H ₂O) use light microscope to observe after the etching.

Case-hardened representative industrial sample is used by obtaining and do metallographic research along the horizontal and vertical cutting of welding bead among Fig. 7.Fig. 8 a and Fig. 8 b are the micro-structural of horizontal and vertical direction cutting sample, show nascent M after the sour iron chloride etching ₇C ₃The existence of carbide represents that high chromium white iron is hypereutectic composition.The chemical ingredients of hardened surface shown in Figure 7 from sample I as shown in Table V, the composition of the hardened surface of other industrial sample is from sample II and sample III.

Table V Industrial hardened 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 industrial sample common characteristic of observing is to have crackle to produce, all samples all contain the crackle of 5～10mm eyed structure in the whole zone of surface hardening, most of crackle can extend to the separation surface of matrix and hardened surface, under the certain situation, crackle can be along matrix and further fork and the expansion of hardened surface separation surface, and the enlarged meeting of crackle causes the hardened surface overlay area to be separated with matrix surface on these interfaces.

The microstructure of coverage rate can promote wearing character, and it is very important for optimizing polishing machine.The covering micro-structural that detects in the sample is hypereutectic high-chromium white iron micro-structural, and this micro-structural is by the nascent M in the austenite eutectic composition ₇C ₃Carbide connecting rod and eutectic M ₇C ₃Carbide forms.But the microstructure of detection also comprises bad feature, as the interconnected carbide of complex rule.

The desired microstructure that Fig. 9 applies the surface for the sclerosis weldering.Fig. 9 comes from the sample II in the Table V, but is not the representative of this sample or other samples.Micro-structural among Fig. 9 is the etching of peracid iron chloride, and micro-structural comprises M ₇C ₃Nascent M in carbide and the austenite eutectic matrix ₇C ₃The hexagonal bar of carbide (white), when the latticed austenite ring of light was visible around the primary carbide, the primary carbide bar was almost vertical with plane shown in Fig. 9, so it seems to be almost hexagon.The profile of carbide bar changes with the difference of their directions, so primary carbide is an elongated rod shape when extending vertically up to the plane that Fig. 9 takes, rather than sexangle.

The material melt undercooling is but the time, that is to say that liquid cools off with subnormal temperature of solidification before solidifying, can not produce normal eutectic phenomena shown in Figure 9, but take among the sample III of Table V, the interconnective fork of carbide bar is arranged in the austenite shown in Figure 10.Microstructure among Figure 10 is the representative of all samples, comprises the sample II of under-represented microstructure shown in Figure 9.

Eutectic among Figure 10 after sour iron chloride etching is still by M ₇C ₃Carbide bar (white) and austenite mixed form, and carbide bar direction is substantially parallel with zone shown in Figure 10.This supercooled eutectic is called the eutectic of complex rule, and the diameter of eutectic bar is about 1/5th of the bar of primary carbide shown in Fig. 9, and triple rotational symmetry structures are arranged, and this can cause carbide group's trilateral outward appearance.Because interconnecting of these eutectic bars, this microstructure provide long interconnective path for crackle enlarges.Therefore the micro-structural among Figure 10 is bad structure, although its high chromium white iron weldering before the present invention is very common in applying.

The etching sample is carried out finding behind EBSD (EBSD) and the X-ray diffraction carbide bar of equilateral triangle is interconnected in all complex rule eutectics, wherein, the carbide bar of complex rule is M ₇C ₃, its hexagonal transverse cross section and nascent M ₇C ₃The cross section of carbide is identical, although the carbide of complex rule is better, is about five times of primary carbide, and " particle " of this complex rule structure in millimeter is common.Figure 11 a and Figure 11 b have shown that in detail crackle among the sample II passes the situation of the microstructure of this complex rule.

Because interconnecting of carbide bar greatly reduces in the eutectic, Fig. 9 has shown more preferably eutectic micro-structural, and is equally like this to sample II, and this micro-structural has comprised eutectic M ₇C ₃Nascent M in carbide and the austenite mixed matrix ₇C ₃Bar, and do not have micro-structural with the complex rule of interconnective carbide.

Carbide Phases connects in other high chromium white iron micro-structurals, and facilitates hypereutectic high-chromium white iron to carry out when metal is deposited embrittlement taking place, and this is because contain the nascent M of fork in the structure ₇C ₃The nascent M of carbide (such as the sample III of Figure 12) or fork ₇C ₃With the mixture (the sample III of Figure 13) of complex rule structure, the silicone content or the raising cooling velocity that increase in the alloy generate this two kinds of structures easily.

As mentioned above, when silicone content is high, and the speed of cooling that inherent is exceedingly fast can cause overcooled weldering to apply the time, all generating the primary carbide of fork and the microstructure of complicated rule easily, the growth of these carbide is not to be decided by thermograde but overcooled degree.Overcooling is easier to occur in the zone of closing on matrix, so the direction of these carbide growths is parallel with matrix rather than vertical with matrix, if the growth of carbide can be controlled by thermograde, to be exactly that we are desired see then above-mentioned situation.

The crackle that this has occurred when having explained the industrial sample surface hardening.Among Fig. 7, crackle occurs in the form of covering surfaces with grid, although these crackles are generating near matrix surface, therefore the crackle that appears at covering surfaces can expand covering surfaces to from matrix always, and this crack pattern is the consequence that weld seam solidifies the unrelieved stress effect generation when arranging with the carbide bar.Away from matrix, carbide may be parallel to thermograde and grow, and just grows perpendicular to the direction of matrix.

The electron micrograph sector-meeting that examines Figure 14 is further explained.That shown in Figure 14 is sample III, and it is the deposited tectal electron microscopic picture of high chromium white ferrous metal among sample I, II and the III, and shows with high-amplification-factor.Although Figure 14 is eutectic carbides and austenitic picture, situation is identical with primary carbide in the austenitic matrix.

The front has illustrated that the crackle in high chromium white iron tectum generally can take place along carbide and austenite separation surface, this thin dark colour zone around carbide particle (showing thick less than 0.2 μ m among Figure 14) is a skim martensite, martensitic needles can extend to austenite from these thin layers, the fragility martensite that carbide particle is arranged on every side is under the unrelieved stress effect, for crack propagation provides the ideal path.When not having Malpighian layer, harder austenite can absorb these residual stress, therefore at M ₇C ₃On carbide and the austenite interface, just crackle can not appear.

Reach a conclusion thus, have the primary carbide of fork or complex rule structure (both containing interconnective carbide) or exist martensite all can promote crackle to generate at carbide austenite interface.If can eliminate these factors, when applying, weldering also can eliminate crackle.

It is deposited to use plasma transferred arc (PTA) that two hypoeutectic high chromium white iron are welded on the low-carbon (LC) steel disk, and shown in the Table VI is the powder composition.

Table VI Composition of the present 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 find that the deposited constituent structure effect of this weldering is splendid.Figure 15 is the pictures taken that the sample section is applied in two-layer weldering, and each sample section is that typical weldering is applied.Can see among the figure that the smooth surface that weldering is applied has gloss, does not have slag and does not have surface crack.In addition, when magnet is applied near weldering, the ferromagnetic attraction phenomenon that signifies that martensite exists can not appear.

More than mainly concentrate on nascent M about the narration (corresponding to Figure 14 with Fig. 7) of sample I, sample II and sample III ₇C ₃The interconnective adverse effect of carbide.Yet, as shown in figure 14, in those samples at M ₇C ₃Carbide and Austenite Interfacial can detect martensite and exist, among sample I, II and the III each also therefore and show strong ferromagnetism that is to say, sample I, sample II and sample III carry out metal deposited after, can produce powerful attraction 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 do not have crackle to produce fully during weldering is applied.The characteristics of micro-structural are inner tree-shaped crystalline substance and M ₇C ₃And austenitic eutectic, and at M ₇C ₃There are not martensite in carbide and austenite interface, in addition, and M ₇C ₃The degree that interconnects of carbide is also lower.Two kinds of powder cause the dilution of fabulous flowability and about 10%～25%.Matrix needs pre-heated degree also to be significantly less than prior art in the invention, about 150 ℃ rather than 300 ℃.

At last, we welcome the above embodiment is carried out other modifications and corrigendum within the scope of the present invention.

Claims (28)

1. an anti-wear high chromium white iron is characterized in that described white iron has a kind of micro-structural in the situation without Overheating Treatment, contain austenite and M in the micro-structural ₇C ₃Carbide, contain at least a martensite promoter and at least a austenite stabilizer in the described white iron, and the content of described martensite promoter and austenite stabilizer reaches separately level so that effect balance between the two, thereby makes white iron not have crackle.

2. anti-wear high chromium white iron according to claim 1 is characterized in that in the described white pig iron that at least a martensite promotor is that silicon or boron or both are used in combination.

3. anti-wear high chromium white iron according to claim 1 is characterized in that at least a martensite promotor in the described white pig iron is content at 0.25%～3.5% silicon.

4. anti-wear high chromium white iron according to claim 1 is characterized in that at least a martensite promotor in the described white pig iron is content at 0.5%～3.25% silicon.

5. anti-wear high chromium white iron according to claim 1 is characterized in that at least a martensite promotor is the boron of the Gao Yueda 2% of content in the described white pig iron.

6. anti-wear high chromium white iron according to claim 1 is characterized in that at least a martensite promotor is the boron of the Gao Yueda 1% of content in the described white pig iron.

7. according to the described anti-wear high chromium white iron of arbitrary claim in the claim 1 to 6, it is characterized in that at least a austenite stabilizer is manganese or nickel or copper or molybdenum in the described white pig iron.

8. anti-wear high chromium white iron according to claim 7, it is characterized in that at least a austenite stabilizer in the described white pig iron is content at 4%～12% manganese or nickel or copper or the molybdenum of equivalent effect is arranged, and the content of this molybdenum does not comprise and generates the part that carbide takies.

9. anti-wear high chromium white iron according to claim 7, it is characterized in that at least a austenite stabilizer in the described white pig iron is content at 4%～8% manganese or nickel or copper or the molybdenum of equivalent effect is arranged, and the content of this molybdenum does not comprise and generates the part that carbide takies.

10. according to the described anti-wear high chromium white iron of arbitrary claim in the claim 1 to 9, it is characterized in that described white iron is in the casting state, martensite promoter and austenite stabilizer reach the balance of effect between the two with content separately, like this, and the austenite of white iron and M ₇C ₃There is not martensite in the carbide interface.

11., it is characterized in that described white pig iron contains the hardened surface that metal is deposited on matrix surface after deposited, and this hardened surface does not have crackle according to the described anti-wear high chromium white iron of claim 1 to 9.

12. anti-wear high chromium white iron according to claim 11 is characterized in that the mutual effect of martensite promoter and austenite stabilizer reaches balance in the described white iron, like this M of micro-structural ₇C ₃In the carbide carbide particle to interconnect degree relatively low.

13. anti-wear high chromium white iron according to claim 12, it is lower to it is characterized in that in the described white iron that carbide particle interconnects degree, the carbide particle that does not have like this fork in the micro-structural, and martensite promoter and austenite stabilizer reach the balance of effect between the two with content separately, therefore austenite and M in described white iron ₇C ₃There is not martensite in the carbide interface.

14. according to the described anti-wear high chromium white iron of arbitrary claim in the claim 1 to 13, it is characterized in that described white iron is the hypoeutectic state, the interface in the described hypoeutectic structure comprises primary austenite and eutectic M ₇C ₃Interface between the carbide and eutectic austenite and eutectic M ₇C ₃Interface between the carbide.

15. according to the described anti-wear high chromium white iron of arbitrary claim in the claim 1 to 13, it is characterized in that described white iron is the eutectic state, the interface in the described eutectic structure is at eutectic austenite and eutectic M ₇C ₃Between the carbide.

16. according to the described anti-wear high chromium white iron of arbitrary claim in the claim 1 to 13, it is characterized in that described white iron is hypereutectic state, the interface in the described hypereutectic structure comprises nascent M ₇C ₃Interface between carbide and the eutectic austenite and eutectic austenite and eutectic M ₇C ₃Interface between the carbide.

17. according to the described anti-wear high chromium white iron of arbitrary claim in claim 14 and the claim 10 to 14, it is characterized in that carbon content is 1.0%～3.0% in the described white pig iron, chromium content is 18.0%～27.0%, manganese and nickel content be 4.0%～8.0% or both combined content of manganese nickel be 4.0%～8.0%, silicone content is 0.25%～2.75%, also contains ferro element and other alloying elements and impurity in addition.

18. according to the described anti-wear high chromium white iron of arbitrary claim in claim 14 and the claim 10 to 14, it is characterized in that carbon content is 2.5%～4.0% in the described white pig iron, chromium content is 18.0%～27%, manganese or nickel content be 4.0%～8.0% or both combined content of manganese nickel be 4.0%～8.0%, silicone content is 0.25%～2.75%, niobium or vanadium or both combined content mostly are 10% most, also contain ferro element and other alloying elements and impurity in addition.

19. according to the described anti-wear high chromium white iron of arbitrary claim in claim 15 and the claim 10 to 14: it is characterized in that carbon content is 3.0%～4.0% in the described white pig iron, chromium content is 15.0%～27.0%, manganese and nickel content be 4.0%～8.0% or both combined content of manganese nickel be 4.0%～8.0%, silicone content is 0.25%～2.75%, also contains ferro element and other alloying elements and impurity in addition.

20. according to the described anti-wear high chromium white iron of arbitrary claim in claim 15 and the claim 10 to 14, it is characterized in that carbon content is 4.25%～4.75% in the described white pig iron, chromium content is 15.0%～27.0%, manganese or nickel content be 4.0%～8.0% or both combined content of manganese nickel be 4.0%～8.0%, silicone content is 0.25%～2.75%, niobium or vanadium or both combined content mostly are 10% most, also contain ferro element and other alloying elements and impurity in addition.

21. according to the described anti-wear high chromium white iron of arbitrary claim in claim 16 and the claim 10 to 14, it is characterized in that carbon content is 4.0%～5.0% in the described white pig iron, chromium content is 20.0%～27.0%, manganese and nickel content be 4.0%～8.0% or both combined content of manganese nickel be 4.0%～8.0%, silicone content is 0.25%～2.75%, also contains ferro element and other alloying elements and impurity in addition.

22. according to the described anti-wear high chromium white iron of arbitrary claim in claim 16 and the claim 10 to 14, it is characterized in that carbon content is 5.0%～6.0% in the described white pig iron, chromium content is 20.0%～27.0%, manganese or nickel content be 4.0%～8.0% or both combined content of manganese nickel be 4.0%～8.0%, silicone content is 0.25%～2.75%, niobium or vanadium or both combined content mostly are 10% most, also contain ferro element and other alloying elements and impurity in addition.

23., it is characterized in that described white pig iron contains at least two kinds of austenite stabilizers, and total content is no more than 20% according to claim 7 or the described anti-wear high chromium white iron of claim 8.

24., it is characterized in that described white pig iron contains at least two kinds of austenite stabilizers, and total content is no more than 16% according to claim 7 or the described anti-wear high chromium white iron of claim 8.

25. a method of producing anti-wear high chromium white cast iron casting body is characterized in that the high chromium white fusant is poured into a mould, and cools off and obtain by austenite and M ₇C ₃The micro-structural that carbide forms, comprise at least a martensite promoter and at least a austenite stabilizer in the described high chromium white fusant, and the content of martensite promoter and austenite stabilizer reaches level separately so that effect balance between the two avoids the body of casting crackle to occur.

26. produce the method that anti-wear high chromium white iron sclerosis weldering is applied for one kind, it is characterized in that the weldering of high chromium white iron is applied and deposited on the matrix, cooling off then and obtain the sclerosis weldering at matrix at last and apply the surface, the sclerosis weldering is applied the micro-structural on surface by austenite and M ₇C ₃Carbide forms, comprise at least a martensite promoter and at least a austenite stabilizer in the described white iron, and the content of martensite promoter and austenite stabilizer reach separately level so that effect balance between the two avoid the sclerosis weldering to apply the surface and crackle occurs.

27., it is characterized in that the melt described in the method is the melt of the described white pig iron of arbitrary claim in the claim 2 to 9 according to claim 25 or the described method of claim 26.

28., it is characterized in that the effect balance that reaches causes the fracture toughness property of white pig iron to improve between at least a martensite promotor and at least a austenite stabilizer according to claim 25 described method of arbitrary claim to the claim 27.

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