CN111069571A - Endogenetic metal composite of control and pick - Google Patents
Endogenetic metal composite of control and pick Download PDFInfo
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- CN111069571A CN111069571A CN202010084863.7A CN202010084863A CN111069571A CN 111069571 A CN111069571 A CN 111069571A CN 202010084863 A CN202010084863 A CN 202010084863A CN 111069571 A CN111069571 A CN 111069571A
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- 239000002905 metal composite material Substances 0.000 title claims abstract description 35
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 66
- 238000005520 cutting process Methods 0.000 claims abstract description 51
- 229910052742 iron Inorganic materials 0.000 claims abstract description 31
- 238000000034 method Methods 0.000 claims abstract description 31
- 229910052751 metal Inorganic materials 0.000 claims abstract description 26
- 239000002184 metal Substances 0.000 claims abstract description 26
- 239000007788 liquid Substances 0.000 claims abstract description 23
- 229910052684 Cerium Inorganic materials 0.000 claims abstract description 16
- 239000000203 mixture Substances 0.000 claims abstract description 16
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 16
- 238000010791 quenching Methods 0.000 claims abstract description 5
- 230000000171 quenching effect Effects 0.000 claims abstract description 5
- 238000002156 mixing Methods 0.000 claims abstract description 4
- 238000007711 solidification Methods 0.000 claims abstract description 4
- 230000008023 solidification Effects 0.000 claims abstract description 4
- 230000007704 transition Effects 0.000 claims abstract description 4
- 239000002245 particle Substances 0.000 claims description 59
- 239000000463 material Substances 0.000 claims description 24
- 239000002131 composite material Substances 0.000 claims description 21
- 238000004519 manufacturing process Methods 0.000 claims description 14
- 239000003795 chemical substances by application Substances 0.000 claims description 10
- 239000000696 magnetic material Substances 0.000 claims description 3
- 150000001247 metal acetylides Chemical class 0.000 claims 1
- 239000011159 matrix material Substances 0.000 abstract description 23
- 230000008569 process Effects 0.000 abstract description 17
- 238000011065 in-situ storage Methods 0.000 abstract description 14
- 230000004927 fusion Effects 0.000 abstract description 11
- 238000001179 sorption measurement Methods 0.000 abstract description 3
- 238000009826 distribution Methods 0.000 abstract description 2
- 229910034327 TiC Inorganic materials 0.000 abstract 1
- 239000006185 dispersion Substances 0.000 abstract 1
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 28
- 239000000956 alloy Substances 0.000 description 18
- 229910045601 alloy Inorganic materials 0.000 description 16
- 239000000047 product Substances 0.000 description 15
- 238000002360 preparation method Methods 0.000 description 12
- 238000005266 casting Methods 0.000 description 8
- 238000006243 chemical reaction Methods 0.000 description 7
- 230000006872 improvement Effects 0.000 description 7
- 239000010410 layer Substances 0.000 description 7
- 230000007547 defect Effects 0.000 description 6
- 239000003292 glue Substances 0.000 description 6
- 229910001208 Crucible steel Inorganic materials 0.000 description 5
- 238000005299 abrasion Methods 0.000 description 4
- 239000003245 coal Substances 0.000 description 4
- 238000005065 mining Methods 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 229910052721 tungsten Inorganic materials 0.000 description 4
- 239000002699 waste material Substances 0.000 description 4
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 239000006260 foam Substances 0.000 description 3
- 238000007499 fusion processing Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 230000002035 prolonged effect Effects 0.000 description 3
- 238000000926 separation method Methods 0.000 description 3
- 230000036346 tooth eruption Effects 0.000 description 3
- 229910018643 Mn—Si Inorganic materials 0.000 description 2
- 229910000746 Structural steel Inorganic materials 0.000 description 2
- 230000003197 catalytic effect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000013467 fragmentation Methods 0.000 description 2
- 238000006062 fragmentation reaction Methods 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000004321 preservation Methods 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 239000011435 rock Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000013589 supplement Substances 0.000 description 2
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- GYIFSXKTFMKQNG-UHFFFAOYSA-N [Si][Mn][Cr] Chemical compound [Si][Mn][Cr] GYIFSXKTFMKQNG-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000000788 chromium alloy Substances 0.000 description 1
- VNTLIPZTSJSULJ-UHFFFAOYSA-N chromium molybdenum Chemical compound [Cr].[Mo] VNTLIPZTSJSULJ-UHFFFAOYSA-N 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000012217 deletion Methods 0.000 description 1
- 230000037430 deletion Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000003541 multi-stage reaction Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 239000002210 silicon-based material Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000005641 tunneling Effects 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
- 238000009736 wetting Methods 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D19/00—Casting in, on, or around objects which form part of the product
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- E—FIXED CONSTRUCTIONS
- E21—EARTH OR ROCK DRILLING; MINING
- E21C—MINING OR QUARRYING
- E21C35/00—Details of, or accessories for, machines for slitting or completely freeing the mineral from the seam, not provided for in groups E21C25/00 - E21C33/00, E21C37/00 or E21C39/00
- E21C35/18—Mining picks; Holders therefor
- E21C35/183—Mining picks; Holders therefor with inserts or layers of wear-resisting material
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mining & Mineral Resources (AREA)
- Life Sciences & Earth Sciences (AREA)
- General Life Sciences & Earth Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Geology (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The invention discloses an endogenetic-controlled metal composite material, which is prepared by the following steps: mixing low-density hard element carbide TiC, Ce and Mo, and uniformly distributing the mixture at the designated position of a die; pouring iron-based metal liquid with the temperature of 1550-1650 ℃ into a die, preserving heat for not less than 3min, and quenching after solidification to generate the controlled endogenetic metal composite material. The mixture is fixed in position by iron sheet wrapping or magnetic adsorption process. The cutting pick has one integral working end and handle of the cutting pick, and the handle and the working end have transition layer of 1-10 mm and no obvious interface. The invention can promote the in-situ endogenetic fusion of the carbide of the low-density hard element and the matrix material by deleting the active elements, a proper fixing process and a proper pouring process, achieve the uniform dispersion distribution of a hard phase, strengthen the wear resistance of the working end part of the cutting pick, reduce the cost and enlarge the technical application range.
Description
Technical Field
The invention relates to the technical field of mechanical equipment, in particular to a method for controlling endogenetic metal composite material and cutting teeth.
Background
The mining cutting tooth is one of the vulnerable parts in coal mining and roadway tunneling machinery, is a main tool for coal falling and breaking, and has the performance that the performance of the cutting tooth directly influences the exertion of the production capacity of the coal mining machinery, the power consumption, the working stability and the service life of other related parts. The existing cutting pick is manufactured by embedding a hard alloy strip with the diameter of 15-20mm in a hole of the cutting pick tip made of common structural steel materials. Although the hardness of the cemented carbide strip is high, the hardness of the common structural steel material is only about 40 HRC. When the cutting pick head is embedded into a mining layer in actual production, the cutting pick head is abraded due to insufficient wear resistance of a head base material, and the hard alloy strips embedded in the holes in the top end are easy to fall off due to base abrasion, so that the service life is shortened. And the cemented carbide strip is expensive.
In order to overcome the problems of the existing cutting picks, the applicant prepared the cutting pick by the two-fluid composite method disclosed in the previous utility model patent (application No. 201120178148.6, patent name: bimetal composite hammer head), and found that this method has disadvantages: the controllability of the composite process is poor, and the yield is low; the interface has poor wetting, the composite quality is unstable, and the composite material is easy to fatigue fracture and fall off; the production process is complex and the product cost is high.
The applicant also adopts the method that hard alloy particles (the particle size is 0.1mm multiplied by 0.1mm to 20mm multiplied by 20mm) are firstly placed in a mould and then a base material alloy solution is poured to prepare the bimetal composite product in the prior invention patent (application number: 201410455186.X, the patent name: the casting process of the bimetal composite hard alloy particles and the product thereof), and the obtained product can realize the metallurgical combination of the hard alloy material and the base material and has better wear resistance. However, in further practice it has been found that the products according to this solution still exhibit particle shedding of the cemented carbide parts.
The applicant also creates a (Ti, W) Cp/Fe in-situ composite bimetal positioning fusion process and a product, so that the process can meet the requirement of forming dispersive metallurgical fusion in situ between a hard reinforcing phase and a base material, avoid falling and separation, fix the composite material in a designated area, realize local reinforcement (non-surface layer) and meet different performance requirements of different parts of parts. Firstly, in the preparation method, a precast block is needed to fix the hard phase (Ti, W) C and the active element particles, and in the precast block, cold glue is needed to realize the adhesion between the fixed hard phase (Ti, W) C and the active element particles, but the cold glue generates a large amount of gas and waste residues in the high-temperature pouring process of the base material, so that the quality of the fused product is influenced. Secondly, in order to make the density of the hard phase particles basically equal to that of the molten steel of the matrix material in the preparation method, the high-density element W is needed, and the preparation process of the (Ti, W) C particles is complex and the production cost is high. That is to say, the method can not realize the in-situ dispersive metallurgical fusion between the low-density hard phase particles and the matrix material, so that the cutting pick prepared by the process has high cost and is not beneficial to popularization.
Therefore, the cutting teeth prepared by the existing process have the defects of easy abrasion, easy falling or high cost, and the application creates the controlled endogenetic metal composite material and the cutting teeth which have wide material range, can greatly reduce the raw material and process cost, have high wear resistance and are not easy to fall.
Disclosure of Invention
The technical problem to be solved by the invention is to provide a bimetal fusion process for controlling an endogenous metal composite material, which can meet the metallurgical fusion of in-situ diffusibility between a low-density hard phase and a base material and meet different performance requirements of different parts of a part, avoid the falling and separation of hard phase particles, and greatly reduce the cost, thereby overcoming the defects of the existing cutting pick product.
In order to solve the technical problem, the invention provides an endogenetic control metal composite material, and a preparation method of the endogenetic control metal composite material comprises the following steps:
(1) mixing the low-density hard element carbide and the active element particles Ce and Mo, and uniformly distributing the mixture at a specified position in a die;
(2) pouring the smelted iron-based metal liquid into the die, wherein the pouring temperature is 1550-1650 ℃;
(3) and after the pouring is finished and the solidification is finished, quenching to generate the controlled endogenetic metal composite material.
In a further improvement, the low-density hard element carbide adopts hard phase particles TiC, and the density ratio of the hard phase particles TiC to the iron-based metal liquid is 0.6.
The further improvement is that the mixture in the step (1) is wrapped by iron sheet with the thickness less than or equal to 0.3mm, pressed into a required shape and arranged at the designated position of the die.
In a further improvement, the mixture in the step (1) is adsorbed to a designated position of the mold through a magnetic material arranged outside the mold.
Further improvement, in the step (1), the particle size of the hard phase particles TiC and the active element particles Ce and Mo is 10-100 micrometers.
The further improvement is that the mass ratio of the hard phase particles TiC, the active element particles Ce and the active element particles Mo to the mass ratio of the iron-based metal liquid are 5-30%, 0.1-0.15% and 0.6-1.0% respectively.
Further improved, the mixture of the hard phase particles TiC and the active element particles Ce and Mo also comprises a homogenizing agent accounting for 0.3-0.4% of the mass ratio of the iron-based metal liquid.
Further improvement, after the pouring in the step (3) is finished, the negative pressure is stopped for 2-3 minutes, and the temperature in the mold is kept to be not lower than 1550 ℃ within 3 minutes.
Further improvement, the hard phase in the endogenetic metal composite material is controlled to be uniformly dispersed and distributed, and the hardness is HRC 60-65.
The invention also provides a cutting pick which comprises a working end part and a handle part, wherein the working end part and the handle part are integrally prepared and formed by adopting the preparation method for controlling the endogenetic metal composite material, the working end part is the endogenetic metal composite material formed by the preparation method, the handle part is a base material in the preparation method, and a transition layer of 1-10 mm is arranged between the handle part and the working end part, so that no obvious bonding interface exists.
According to the invention, active elements and low-density hard element carbide particles are mixed, an iron sheet coating or magnetic adsorption process is adopted, the active elements are uniformly distributed in a designated area of a die, and then the iron-based metal liquid is poured at a proper pouring temperature for a proper time, wherein the active elements Ce and Mo can play a role in reducing interface energy, reducing element interface tension and improving wettability, and the active elements also have interface enrichment characteristics to form a coating structure, influence the change of interface atomic force, purify a crystal boundary and participate in catalytic interface reaction. The preparation method improves the uniformity of macroscopic distribution and the wettability among microscopic elements, and solves the problems of density difference and uniform fusion between a hard phase and a matrix material.
After adopting such design, the invention has at least the following advantages:
according to the invention, by selecting active elements and adopting a proper mixture fixing method, low-density hard phase TiC particles are mixed with the active elements Ce and Mo, and the iron-based metal liquid is poured, so that simple in-situ diffused fusion of low-density carbide and a matrix material can be realized, the metallurgical bonding of the low-density hard phase and the matrix material is strengthened, and the problem that the in-situ diffused fusion reaction of the low-density carbide and the matrix material cannot be realized in the prior art is overcome, so that the problems of falling and separation of the existing hard phase are effectively avoided, the preparation cost of controlling the endogenous metal composite material is greatly reduced, and the method is favorable for popularization and use.
According to the invention, the low-density hard phase particles TiC and the active element particles Ce and Mo are fixed in the designated area of the die by adopting an iron sheet wrapping or magnetic adsorption process, so that the step of preparing a precast block in the prior art is avoided, the defect that cold glue in the precast block is easy to generate gas and waste residue is avoided, the strength, toughness and wear resistance of the designated part of a bimetal composite product are enhanced, the application range and service life of the cutting pick are improved, the process difficulty and the cutting pick production cost are reduced, and the method is more suitable for popularization and application.
The process method is controllable, suitable for mass production of production lines, low in production cost, high in yield and firm in compounding, and can meet the performance requirements of different parts of mechanical parts.
Detailed Description
The invention aims to solve the technical problem of preparing a controlled endogenetic metal composite material with high wear resistance, difficult shedding and low cost by using low-density hard phase particles. In the embodiment, low-density hard phase particles TiC are taken as an example of a wear-resistant metal material of the cutting pick working end part, a proper active element is selected and mixed with the low-density hard phase particles TiC, and the metal composite cutting pick with the cutting pick working end part and the handle part which are integrally formed is manufactured through high-temperature pouring.
Due to the fact thatThe density of the titanium carbide (TiC) is 4.09-4.903g/cm3And the density of the metal matrix liquid is lower than that of the iron-based metal matrix liquid, the density ratio of the iron-based metal matrix liquid to the iron-based metal matrix liquid is 0.6, segregation is easy to occur during pouring, and the in-situ composite reaction is not facilitated to be promoted. Of course, other low density hard phase particles also suffer from the problems described above.
Active elements are selected through deletion and selection, active element particles Ce and Mo are selected to be mixed with titanium carbide, and the effects of reducing the interface energy, reducing the element interface tension and improving the wettability of the active elements Ce and Mo can be exerted; the active element also has the characteristic of interface enrichment, forms a coating structure, purifies a crystal boundary and can participate in catalytic interface reaction. And the in-situ control reaction of the working end part of the metal composite cutting pick can be realized by fixing the designated positions of the titanium carbide TiC and the active element particles Ce and Mo, so that the metal composite cutting pick with high wear resistance, difficult shedding and low cost is formed. Specific examples are as follows.
Example one
(1) Mixing hard phase particles TiC, active element particles Ce and Mo and a homogenizing agent, and uniformly distributing the mixture at a specified position in a mould.
The active elements Ce and Mo can reduce the interface energy, so that the electronegativity is stronger, the in-situ fusion reaction of the diffusibility is facilitated, and the in-situ fusion of the low-density hard phase TiC and the matrix liquid plays a vital role.
In the embodiment, the particle sizes of the low-density hard phase particles TiC and the active element particles Ce and Mo are both 10-100 micrometers. And the mass of the hard phase particles TiC, Ce, Mo and the homogenizing agent accounts for 5 percent, 0.15 percent, 1.0 percent and 0.3 percent of the mass of the iron-based metal liquid respectively.
In the embodiment, the homogenizing agent is a homogenizing agent commonly used in the field and is used for homogenizing.
In order to avoid the existing cutting pick end part to have a non-wear-resistant material, the cutting pick of the embodiment is integrally divided into a front part and a rear part, the front part is a wear-resistant working end part, and the rear part is a connecting handle part. The mixture of hard phase particles TiC and active element particles Ce, Mo and the homogenizing agent is disposed over the entire front end of the pick die.
The concrete fixing mode in this embodiment is that the mixture is wrapped by iron sheet with thickness less than or equal to 0.3mm, pressed into required shape, and then arranged at the front end part of the cutting pick, namely the working end part of the cutting pick. Because the iron sheet can be melted in the subsequent casting process and becomes a base material in the casting process, the steps of the casting process are not influenced, the positions of the mixed particles of the carbide of the low-density hard element and the active element can be well controlled, and the defect that the preparation process is influenced because cold glue is adopted in the prior art and gas and waste residue are easily generated can be avoided.
The length of pick working end portion is 60 ~ 80mm in this embodiment, and the length of connecting the stalk portion is 30 ~ 120 mm.
(2) And pouring the melted iron-based molten metal into the die at 1650 ℃.
The embodiment adopts the lost foam process to cast the cutting tooth mould. The negative pressure environment is obtained by vacuumizing the closed box body, the foam plastic full mold fixed with the mixture of the hard phase particles TiC, the active element particles Ce, Mo and the homogenizing agent is arranged in the closed box body, and a cavity of the foam plastic full mold is arranged upwards. The closed box body is also filled with precious pearl sand with low thermal conductivity, and has the function of heat preservation.
In this embodiment, the iron-based metal liquid is made of alloy cast steel 30 chromium-manganese-silicon material, and the cutting tooth mold is poured and replaced from bottom to top by the iron-based metal liquid.
(3) After the casting is finished and the cutting tooth is solidified, quenching is carried out to generate the cutting tooth, the working end part of the cutting tooth is made of TiCp/Fe control endogenetic metal composite material, the connecting handle part of the cutting tooth is made of alloy cast steel 30 Cr-Mn-Si material, a transition layer of 1-10 mm is arranged between the handle part and the working end part, and no obvious bonding interface exists.
Wherein the quenching temperature is 850 ℃. In the step, after the pouring is finished, the negative pressure is stopped for 2-3 minutes, and the temperature in the box body is kept to be not lower than 1550 ℃ within 3 minutes; then the negative pressure is started rapidly to achieve rapid cooling.
Thus, the JDK65/36 pick is integrally formed by the controlled-in-place metal fusion process. The cutting pick connecting handle is made of alloy cast steel 30 Cr-Mn-Si material, and the cutting pick working end is made of metal fusion composite material formed by in-situ reaction of iron-based metal, TiC hard phase and active elements. The iron-based metal matrix material is characterized in that titanium carbide is tightly and firmly fused together by a strong martensite matrix, and a supporting protection effect is generated on reinforced phase particles, and the reinforced phase particles supplement each other, so that the performance of a composite material at the working end part is greatly improved, and the service life of a cutting tooth is finally prolonged.
The hardness of the cutting pick working end part formed by the embodiment is HRC60, the wear-resistant composite layer is 35mm, and the total weight is 1.85 kilograms. The cutting pick works on a mixed rock stratum, strong impact is generated in the working process, and the situation that particles are broken does not occur in the wear-resistant part in a cutting pick test.
Example two
The second embodiment is different from the first embodiment in that the specific fixing manner in the first embodiment is that the mixture is adsorbed at the designated position of the mold, namely the working end part of the cutting pick, through the magnetic material arranged outside the mold, and the defect that the preparation process is affected by the fact that cold glue is adopted in the prior art and gas and waste residue are easily generated can be avoided.
In the present example, the mass of the hard phase particles TiC, Ce, Mo and the homogenizing agent was 15%, 0.1%, 0.6% and 0.4% respectively based on the mass of the iron-based metal liquid. The matrix component of the iron-based metal liquid is a low-alloy cast steel 42 chromium-molybdenum material, the casting temperature is 1600 ℃, and the JGC102/35 type cutting pick is produced. The hardness of the working end of the JGC102/35 type pick is HRC 65. The total weight of the cutting pick is 1.75 kilograms, and the wear-resistant composite layer is 40 mm.
The working object of the cutting pick is a strong weathered rock stratum, no strong impact force exists, the abrasion surface is concave-convex, and the positioning reinforced part has no fragmentation phenomenon.
EXAMPLE III
The third embodiment is different from the first embodiment in that the mass of the hard phase particles TiC, Ce, Mo and the homogenizing agent accounts for 30%, 0.15%, 0.8% and 0.4% of the mass of the iron-based metal liquid, respectively. The matrix component of the iron-based metal liquid adopts 40 chromium alloy cast steel, and the casting temperature is 1550 ℃, so that the JGC80/30 type cutting pick is produced. The hardness of the working end of the JGC80/30 type cutting pick is HRC 65. The total weight of the cutting pick is 1.75 kilograms, and the wear-resistant composite layer is 40 mm.
The cutting pick works on a coal seam, no strong impact force exists, the abrasion surface is smooth, and the positioning reinforced part has no fragmentation phenomenon.
Metallographic analysis was performed on the metal composite pick products produced in the above product examples 1 to 3. And (3) metallographic display: the matrix structure of each product is martensite and a small amount of retained austenite, the carbide hard phase is uniformly distributed, a large amount of TiC can be seen on the hard alloy structure and the matrix of the fusion bonding layer around the hard alloy structure, the reinforcing phase is completely wetted with the high-temperature solution, and the metallurgical bonding between the hard alloy material and the matrix material is realized.
The controlled endogenetic metal composite material produced according to the process plays an obvious role in strengthening a matrix by virtue of the super-strong hardness of the titanium carbide alloy, and hard alloy particle materials are tightly and firmly fused together by the matrix material by virtue of the strong martensite structure of the matrix material, so that the hard alloy particle materials are supported and protected, and the matrix material and the hard alloy particle materials supplement each other, so that the service life of the product is prolonged, and the production cost is reduced.
Compared with the manufacturing process of embedding the hard alloy prefabricated block body in the base material adopted in the prior art, the invention emphasizes the characteristics of reducing the interface energy, improving the wettability and the electronegativity of the material by active elements, improving the nucleation force and the in-situ reaction bonding force of crystals, lightening the segregation of the enhanced phase, realizing the uniform distribution of the enhanced phase, and the metallurgical bonding of the titanium carbide enhanced phase and the base material, effectively avoiding the phenomena of falling and breaking of the hard phase and overcoming the defect of gas generation in the prior prefabricated block when cold glue meets high temperature. The invention adopts the high heat preservation and quick solidification process in the production process, so that the base material of the non-reinforced part and the reinforced part form the bimetal composite, the performance requirements of different parts of mechanical parts are met, the in-situ composite technology and the bimetal positioning casting process are combined into a whole, the wear resistance and the application range of the bimetal composite product are improved, and the service life of the bimetal composite product is prolonged.
The TiCp/Fe controlled endogenetic metal composite cutting pick has the advantages that the front end part of the TiCp/Fe controlled endogenetic metal composite cutting pick is made of a controlled endogenetic metal composite material with good wear resistance, the problem that the existing cutting pick head base body material is poor in wear resistance can be solved, the TiC cost is low, the preparation cost of the cutting pick can be greatly saved, the process steps are simplified, and the popularization is facilitated.
The above description is only for the purpose of illustrating the preferred embodiments of the present invention and is not to be construed as limiting the present invention in any way, and it will be apparent to those skilled in the art that the above description of the present invention can be applied to various modifications, equivalent variations or modifications without departing from the spirit and scope of the present invention.
Claims (10)
1. The method for preparing the controlled endogenesis metal composite material is characterized by comprising the following steps:
(1) mixing the low-density hard element carbide and the active element particles Ce and Mo, and uniformly distributing the mixture at a specified position in a die;
(2) pouring the smelted iron-based metal liquid into the die, wherein the pouring temperature is 1550-1650 ℃;
(3) and after the pouring is finished and the solidification is finished, quenching to generate the controlled endogenetic metal composite material.
2. An endogenetic controlled metallic composite according to claim 1, characterized in that the low density hard element carbides employ hard phase particles TiC, the density ratio of which to the iron based metallic liquid is 0.6.
3. The controlled endogenetic metal composite of claim 2, wherein in step (1) the mixture is wrapped with iron sheet with thickness less than or equal to 0.3mm, pressed into a desired shape and placed at a designated position of a mold.
4. The controlled endogenetic metallic composite of claim 2, wherein the mixture of step (1) is adsorbed at a designated position of the mold by a magnetic material disposed outside the mold.
5. The controlled endogenetic metal composite of claim 2, wherein the grain size of the hard phase particles TiC and the active element particles Ce and Mo in step (1) is 10 to 100 μm.
6. The controlled endogenous metal composite of claim 5, wherein the mass ratios of the hard phase particles TiC, active element particles Ce and active element particles Mo to the iron-based metal liquid are 5-30%, 0.1-0.15% and 0.6-1.0%, respectively.
7. The controlled endogenic metal composite material of claim 6, wherein the mixture of the hard phase particles TiC and the active element particles Ce and Mo further comprises a homogenizing agent accounting for 0.3-0.4% of the mass ratio of the iron-based metal liquid.
8. The controlled endogenous metal composite of claim 1, wherein after the pouring in step (3) is completed, the negative pressure is stopped for 2-3 minutes, and the temperature inside the mold is kept at 1550 ℃ or higher within 3 minutes.
9. The controlled endogenetic metal composite according to any of the claims 1 to 8, wherein the hard phase in the controlled endogenetic metal composite is uniformly dispersed and has a hardness of HRC 60-65.
10. A cutting pick, characterized in that the cutting pick comprises a working end part and a shank part, the working end part and the shank part are integrally manufactured and formed by the method for manufacturing the controlled endogenetic metal composite material according to any one of claims 1 to 9, the working end part is the controlled endogenetic metal composite material formed by the method for manufacturing, the shank part is a base material in the method for manufacturing, and a transition layer of 1-10 mm is arranged between the shank part and the working end part, and no obvious bonding interface is formed.
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| CN202571249U (en) * | 2012-03-29 | 2012-12-05 | 江苏兄弟活塞有限公司 | Mold for producing piston embedded with steel piece |
| CN103341614A (en) * | 2013-06-27 | 2013-10-09 | 重庆罗曼耐磨材料有限公司 | Simple method for manufacturing ceramic-metal composite wear-resistant part |
| CN109504889A (en) * | 2019-01-04 | 2019-03-22 | 孙岗 | (Ti, W) Cp/Fe in-situ composite bimetallic positioning fusion process and product |
| CN110385421A (en) * | 2018-04-18 | 2019-10-29 | 朝阳多元双金属复合制造有限公司 | A kind of complex method twice of the anti-wear-resisting ZG35GrMnSi steel part that breaks |
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| JPH02137660A (en) * | 1988-11-18 | 1990-05-25 | Sintokogio Ltd | Production of ceramics internal chill body |
| CN202571249U (en) * | 2012-03-29 | 2012-12-05 | 江苏兄弟活塞有限公司 | Mold for producing piston embedded with steel piece |
| CN103341614A (en) * | 2013-06-27 | 2013-10-09 | 重庆罗曼耐磨材料有限公司 | Simple method for manufacturing ceramic-metal composite wear-resistant part |
| CN110385421A (en) * | 2018-04-18 | 2019-10-29 | 朝阳多元双金属复合制造有限公司 | A kind of complex method twice of the anti-wear-resisting ZG35GrMnSi steel part that breaks |
| CN109504889A (en) * | 2019-01-04 | 2019-03-22 | 孙岗 | (Ti, W) Cp/Fe in-situ composite bimetallic positioning fusion process and product |
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