CN111424205B - Method for improving wear resistance of high-chromium cast iron alloy by adopting microalloying engineering - Google Patents
Method for improving wear resistance of high-chromium cast iron alloy by adopting microalloying engineering Download PDFInfo
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- CN111424205B CN111424205B CN202010356927.4A CN202010356927A CN111424205B CN 111424205 B CN111424205 B CN 111424205B CN 202010356927 A CN202010356927 A CN 202010356927A CN 111424205 B CN111424205 B CN 111424205B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/08—Making cast-iron alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C1/00—Refining of pig-iron; Cast iron
- C21C1/08—Manufacture of cast-iron
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D5/00—Heat treatments of cast-iron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
- C22C37/06—Cast-iron alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
- C22C37/10—Cast-iron alloys containing aluminium or silicon
Abstract
The invention discloses a method for improving the wear resistance of a high-chromium cast iron alloy by adopting microalloying engineering, which comprises the following steps of taking 0.10-0.25% of aluminum, 1.0% of copper-zinc alloy and rare earth alloy as modifiers, carrying out pre-pearlite treatment by keeping the temperature at 650 ℃ for 5 hours and carrying out austenitizing-microalloying heat treatment by keeping the temperature at 920 ℃ for 2 hours and keeping the temperature at 950 ℃ for 8-10 hours, refining elements of eutectic carbide, improving the form of cast eutectic carbide, improving the yield of products and solving the problem of high brittleness of castings of the high-chromium cast iron alloy; and the grain boundary distribution is optimized to obtain the grain boundary sigma 1 lath martensite with small angle, so that the wear resistance of the alloy is improved, the precipitation amount of secondary carbides in a matrix is increased in the grain boundary optimization process, the carbon content of austenite is reduced, the lath martensite transformation amount is increased, the toughness of the material is increased, and the wear resistance of the material is obviously improved.
Description
Technical Field
The invention relates to the technical field of metallurgical casting, in particular to a method for improving the wear resistance of a high-chromium cast iron alloy by adopting microalloying engineering.
Background
The Cr15 high-chromium cast iron is Cr15 high-chromium cast iron developed by Climax molybdenum industry of America, the Mo content in the components of the Cr15 high-chromium cast iron is 3%, the Cr15Mo3 high-chromium cast iron becomes the best-known wear-resistant white cast iron, and the cast iron is applied to manufacturing impurity pump flow-through parts by Shenyang casting research institute and Shijiazhuang water pump plant in the earliest 80 th century of China. However, in the components of the Cr15Mo3 wear-resistant white cast iron, because the Mo content is high and the cost of the alloy is also high, the technical scheme of Cr15 high-chromium cast iron using manganese to replace molybdenum is researched successively, the research is earlier Russian, in the mark ч х 22 of the standard of alloy iron casting (r ^ The. E7769-, the hardness of the alloy is improved, and Cr15 high-chromium cast iron with manganese replacing molybdenum is applied to manufacturing of impurity pump flow-through components. And the mechanism of reducing the retained austenite amount by pretreatment quenching is shown in the research process, after the pretreatment quenching, the uneven distribution of manganese is mainly caused by the pretreatment, the pretreated structure is mainly pearlite and is distributed in a lamellar manner, the manganese is mainly gathered in a carburized body area, and the carbon content in the ferrite is relatively low. Upon quenching, the numerous low manganese regions increase the Ms point, resulting in a decrease in retained austenite.
Along with the competition of the high-chromium iron casting market, higher requirements for reducing the cost of the high-chromium iron casting are put forward, so that research on Cr15 high-chromium iron without molybdenum is started, in this respect, Morphe Zhenshi et al, for 1.69-3.40C-15 Cr-1.0-3.0 Mn-1.0-2.0 Cu alloy, heat preservation is carried out at 1000 ℃ for 360ks, then quenching is carried out, and the influence of Mn, Ni and Cu on MS points is researched; from the perspective of alloy hardenability, Tang Chong et al have demonstrated that Cr15 high-chromium cast iron can be completely substituted for molybdenum with 6.0% manganese. In practical application, the molybdenum-free Cr15 high-chromium cast iron is applied to a ball mill lining plate and a crusher tooth plate. Although the Cr15 alloy with manganese replacing molybdenum solves the problem of much retained austenite by heat treatment, namely the Cr15Mo3 level can be basically reached from the aspect of hardness, the Cr15 alloy also has certain problems in the aspect of manufacturability; the problems in the manufacturability are mainly that the austenite in the cast structure is coarse, and eutectic carbide (Fe, Cr, Mn) containing manganese is generated7C3. And eutectic carbide (Fe, Cr, Mn)7C3Eutectic carbide (Fe, Cr) of Cr15Mo37C3Fast growth, strong directionality, long sheet, high connectivity eutectic carbide (Fe, Cr, Mn)7C3This results in a material having a high brittleness in the as-cast state and easily causing a crack defect.
The method for solving the problem of poor manufacturability is to select good alterant, improve the solidification condition, refine primary crystal austenite and refine eutectic carbide (Fe, Cr, Mn)7C3. For molybdenum-free Cr15Mn series highThe chromium cast iron is modified by selecting V, Ti, RE, Zn and other elements as modifier, and has good effect. In the prior art, studies on microalloying elements on high-chromium cast iron are mostly limited to alloying, modification and the like of the high-chromium cast iron, and mainly improve the form of eutectic carbide, but no studies on improving the wear resistance of the high-chromium cast iron by microalloying engineering are found.
Although eutectic carbides (Fe, Cr, Mn)7C3Micro-hardness ratio of (1) to eutectic carbide (Fe, Cr)7C3But factors affecting wear resistance during use have a large relationship with the micro-hardness of the matrix in addition to the micro-hardness of the eutectic carbide. Therefore, the problem to be solved by those skilled in the art is how to provide a method to improve the microhardness of the matrix and thus improve the overall wear resistance of the high-chromium alloy.
Disclosure of Invention
In view of the above, the invention provides a method for improving the wear resistance of a high-chromium cast iron alloy by utilizing a microalloying engineering, wherein microalloying elements are added into molten iron of the high-chromium cast iron, the microalloying elements have an inoculation modification effect in the casting solidification process, and the microalloying elements play a special role in the austenitizing process of the high-chromium cast iron to promote secondary carbides to be dispersed and separated out from austenite, reduce the carbon content in the austenite and improve the martensite transformation quantity, so that the form of eutectic carbides is improved, the microhardness of a matrix is improved, and the wear resistance of the high-chromium cast iron is improved.
In order to achieve the purpose, the invention adopts the following technical scheme:
a method for improving the wear resistance of high-chromium cast iron alloy by utilizing microalloying engineering comprises the following steps:
(1) weighing raw materials according to the chemical component proportion requirement, placing the raw materials in an induction furnace, heating until the raw materials are completely melted, and removing impurities to obtain molten iron;
(2) mixing aluminum, copper-zinc alloy and rare earth alloy as an alterant;
(3) adding the alterant in the step (2) into a casting ladle, pouring the molten iron in the step (1) into the casting ladle, stirring and slagging, and preparing for casting, wherein the casting temperature is controlled at 1380-1410 ℃;
(4) and carrying out segmented heat preservation treatment on the poured material for 13-15 hours.
Preferably, the chemical composition ratio of the molten iron in the step (1) is configured according to the chemical compositions required by BTMCr2, BTMCr8, BTMCr15, BTMCr20 or BTMCr 25.
Preferably, the molten iron in the step (1) is prepared by raw materials according to chemical components required by BTMCr15, and specifically comprises the following components of 2.7-2.9 wt% of C, 0.4-0.7 wt% of Si, 2.4-3.0 wt% of Mn, 15-18 wt% of Cr, 0.9-1.1% of Cu, <0.06wt% of S, <0.10wt% of P, 0.07wt% of B, and the balance of Fe.
Preferably, in the step (2), molten iron is used as a metering reference, 0.1-0.25 wt% of aluminum and 1.0wt% of copper-zinc alloy are added, wherein the copper content in the copper-zinc alloy is 87wt%, the zinc content in the copper-zinc alloy is 13wt%, and the added rare earth alloy is a mixture of 0.4wt% of YBZW-4 alloy and 0.2wt% of No. 2 rare earth ferrosilicon alloy or 0.13-0.18 wt% of YBZW-2 alloy.
The beneficial effects of the preferred technical scheme are as follows: al and Y can form Al with a melting point of 1480 DEG C2Y intermetallic compound or high melting point Al formed by Al and Ce4The Ce intermetallic compound can be used as a nucleation particle of austenite to refine the austenite; zn is a surface active element, and after carbide crystallization nucleation, Zn is gathered around the front liquid phase of the carbide or close to the surface of a crystal nucleus, so that the free energy of the front growth part of the carbide is increased, the growth speed of the carbide is hindered, and the sharp angle is rounded.
Preferably, the heat preservation and heat treatment process in the step (4) is as follows: and (3) keeping the temperature at 650 ℃ for 5h, then heating to 920 ℃ and keeping the temperature for 2h, and finally heating to 950 ℃ and keeping the temperature for 8-10 h.
The beneficial effects of the preferred technical scheme are as follows: the cast retained austenite is transformed into pearlite after being kept at 650 ℃ for 5 hours, the components of the cast retained austenite are not changed greatly during austenitizing, the contained carbon is more, the retained austenite is easy to generate when the austenite is transformed into martensite, and the microhardness of a matrix is reduced; when pearlite is austenitized, the pearlite is recrystallized into an austenite structure, so that the components of austenite are relatively homogenized, and the amount of retained austenite is reduced when the austenite is transformed into martensite;
the microalloying engineering step is carried out by keeping the temperature at 920 ℃ for 2 hours and keeping the temperature at 950 ℃ for 8-10 hours, and the specific principle is as follows:
in microalloying engineering, Al element dissolved in austenite has high atom free energy and easy generation of vacancy due to low melting point, Al atom diffuses in austenite according to vacancy diffusion mechanism, Al element is strong graphitizing element and promotes carbon atom segregation during intragranular diffusion, and the segregated C atom is favorable for forming M7C3The secondary carbide is formed, the number of the secondary carbide is increased, and the secondary carbide is dispersed and distributed in a crystal boundary and a crystal;
secondly, in the microalloying engineering, a Zn element is dissolved in austenite in a solid solution mode, and because the boiling point (910 ℃) of the Zn element is lower than the heat treatment temperature, the free energy of atoms is very high, and vacancies are easily generated, and Zn is easily deviated at crystal boundaries, dislocation and fault positions according to a vacancy diffusion mechanism, and is deviated at Zn atoms at the fault positions to form Suzuki gas clusters, so that the austenite fault energy is reduced;
in the microalloying engineering, Y, Ce element which is dissolved in austenite in a solid solution mode generates distortion energy because the radius of the Y, Ce element is larger than that of an iron atom, so that the free energy of Y, Ce atoms is increased, and vacancies are easily generated, and Y, Ce atoms are easily deviated on crystal boundaries, dislocations and stacking faults according to a vacancy diffusion mechanism, so that the austenite stacking fault energy is reduced;
when the stacking fault region and the stacking fault adjacent region are simultaneously partially aggregated with Zn and Y atoms, the Zn and the Y atoms are easy to form covalent bonds, the capability of reducing the stacking fault energy of austenite is increased, the transformation from austenite to lath martensite is promoted, the number of lath martensite is increased, and the Ce atom also has the functions of reducing the stacking fault energy of austenite and increasing the lath martensite.
Fourthly, the alloy is kept at 920 ℃ for 2 hours, secondary carbides can be more easily precipitated, and the carbon content in austenite is reduced, so that the stacking fault energy of the austenite is reduced, and lath martensite is favorably formed.
The invention also claims the high-chromium alloy prepared by the method of the technical scheme and the application of the high-chromium alloy, and the high-chromium alloy is applied to the manufacture of abrasion-resistant iron castings, in particular to overflowing parts of impurity pumps, such as impellers, sheaths, guard plates and the like.
As can be seen from the above technical solutions, compared with the prior art, the present invention has the following technical effects:
first, in order to reduce the burden cost, high-chromium cast iron alloys contain a large amount of Mn, eutectic carbides (Fe, Cr, Mn)7C3The alloy is in a net shape, so that the brittleness of the material in an as-cast state is high, elements capable of inoculating and modifying and refining eutectic carbide are added through selection of modifier elements, the form of the eutectic carbide is improved, the finished product rate of the product is improved, and the problem of high brittleness of a casting of the high-chromium cast iron alloy is solved;
secondly, in the invention, the grain boundary distribution is optimized by combining microalloying engineering and heat treatment to obtain the sigma 1 lath martensite with small angle grain boundary, so that the wear resistance of the alloy is improved, and by the optimization detection of the grain boundary characteristic distribution of the RTMCr25 material sample which is prepared by adopting the technical scheme of the invention and has a structure similar to GX15, the detection result shows that: in the area close to the core part of the sample, ferrite (note: actually lath martensite) grains have preferred orientation, and the normal directions of the {011} planes are parallel to the observation plane, namely parallel to the axial direction of the bar; the {011} oriented crystal grains are close in orientation, so that small-angle crystal boundaries are formed among the {011} oriented crystal grains, the small-angle crystal boundaries are close to the surface (edge) of the bar, the preferred orientation disappears, and no special change rule exists in the area from the center of the bar sample to the surface; in the grain boundary optimization process, the precipitation amount of secondary carbides in a matrix is increased, the carbon content of austenite is reduced, the lath martensite transformation amount is increased, the toughness of the material is increased, and the wear resistance of the material is obviously improved; because the content of chromium in austenite of RTMCr25 is higher than that of GX15, secondary carbon precipitation is more difficult, lath martensite is more difficult to form, and the detection result shows that lath martensite can be formed in RTMCr25, so that the lath martensite can be formed by materials with lower chromium content such as GX 15.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, it is obvious that the drawings in the following description are only embodiments of the present invention, and for those skilled in the art, other drawings can be obtained according to the provided drawings without creative efforts.
FIG. 1 is a drawing showing an as-cast metallographic structure of GX15 obtained in example 1 of the present invention;
FIG. 2 is a graph showing an as-cast characterization of the material produced in comparative example 1 of the present invention;
FIG. 3 is a diagram showing a material obtained in example 1 of the present invention after an austenitizing-microalloying treatment;
FIG. 4 is a metallographic structure of a material obtained in comparative example 2 of the present invention;
FIG. 5 is a metallographic structure of a material obtained in example 2 of the present invention;
FIG. 6 is a graph showing the microhardness of the substrate of the material produced in example 2 of the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
The method for improving the wear resistance of the BTMCr15Mn3Cu1(GX15) alloy by utilizing microalloying engineering comprises the following steps:
(1) weighing raw materials according to the following components of 2.7-2.9 wt% of C, 0.4-0.7 wt% of Si, 2.4-3.0 wt% of Mn, 15-18 wt% of Cr, 0.9-1.1 wt% of Cu, less than 0.06wt% of S, less than 0.10wt% of P, 0.07wt% of B and the balance of Fe, placing the raw materials in an induction furnace, heating until the raw materials are completely melted, removing impurities and obtaining molten iron;
(2) taking molten iron as a measuring standard, mixing 0.2wt% of aluminum, 1.0wt% of zinc-copper alloy (copper 87wt%, zinc 13 wt%) and 0.3 wt% of YBZW-4 refined, 0.2wt% of No. 2 rare earth ferrosilicon alloy as an alterant;
(3) adding the alterant in the step (2) into a casting ladle, pouring the molten iron in the step (1) into the casting ladle, stirring, slagging, and casting at 1380-1410 ℃;
(4) and (3) preserving the heat of the cast at 650 ℃ for 5h, then heating to 920 ℃ and preserving the heat for 2h, finally heating to 950 ℃ and preserving the heat for 8h, and then discharging and cooling by air.
The specific representation diagram of the obtained BTMCr15Mn3Cu1(GX15) alloy is shown in attached figures 1 and 3; FIG. 1 is a metallographic structure drawing of the as-cast state in example 1, in which a modifier is used which is a composite modifier inoculant of 0.2% Al deoxidation, 0.1% Cu-Zn alloy, 0.3% YBZW-4 refining and 0.2% No. 2 rare earth Si-Fe alloy, so as to obtain the as-cast state (Cr, Mn)7C3The form is greatly improved; FIG. 3 is a metallographic structure of a sample 20mm × 20mm × 120mm prepared in example 1, which was subjected to a microalloying-austenitizing treatment at 650 ℃ and 950 ℃ for 8 hours, and had a macro hardness of 62 to 64 HRC; the microhardness of the matrix is 858, 824 and 894 HV.
Comparative example 1
The material obtained in the embodiment of "behavior and action of manganese and molybdenum in high-chromium cast iron" (Chenhuifen. northeast university Master academic paper 1994) was used as comparative example 1, wherein the sample composition comprises the following components in percentage by weight: 3.38% of C, 15.16% of Cr, 0.80% of Si, 0.71% of Mo and 3.34% of Mn; as-cast state (Cr, Mn)7C3The form is shown in figure 2.
Comparative example 2
BTMCr15Mn3Cu1(GX15) was prepared using the preparation protocol of example 1, except that the incubation process was as follows: raising the austenitizing temperature to 1030 ℃, preserving heat for 12h, then lowering the temperature to 970 ℃, preserving heat for 2h, then discharging from the furnace and air cooling, wherein the representation diagram of the obtained substance is shown in figure 4; it is evident from FIG. 4 that the amount of precipitation of secondary carbides between eutectic carbides is small.
Example 2
Example 2 was carried out based on example 1, with the aim of further improving the eutectic carbide morphology and increasing the hardness of GX 15. The method comprises the following steps:
(1) melting qualified molten iron forming GX 15;
(2) adding 0.2% of Al, 0.1% of copper-zinc alloy and 0.13wt% of YBZW-2 alloy as a composite modifier into the step (1), carrying out furnace front treatment, and pouring a guard plate;
(3) carrying out pretreatment on the guard plate prepared in the step (2) at 650 ℃ for 5.0 h;
(4) and (4) carrying out microalloying-austenitizing treatment on the guard plate treated in the step (3) at 920 ℃ for 2h → 950 ℃ for 8h, discharging and air cooling.
The sheet obtained after the above treatment, the produced GX15 material sheet, the macro Hardness (HRC) measured in the factory: 66.8, 64.7, 62.6, a minimum improvement of 3HRC over the 59.4HRC plant test panel hardness produced in example 1.
Sampling the guard plate processed in the steps, wherein the metallographic structure of the guard plate is shown in the attached figure 5, and the hardness detection position of the guard plate is shown in the attached figure 6; as can be seen from fig. 5 and 6, the eutectic carbide morphology is better than that of example 1 (fig. 3); detecting the microhardness of the base body sampled from the guard plate to be 968, 1046 HV;
through the comprehensive analysis of the attached figures 1-6, the following results can be obtained: for RTMCr15Mn3Cu1 high-chromium wear-resistant cast iron, the compound inoculant of the embodiment 1 is adopted, 0.2 percent of Al, 0.1 percent of copper-zinc alloy,
0.3 percent of YBZW-4 is refined, and 0.2 percent of No. 2 rare earth ferrosilicon alloy improves the shape of as-cast eutectic carbide; after the micro-alloying-austenitizing heat treatment of 650 ℃ pretreatment and 950 ℃ maintenance for 8h, the hardness is obviously improved. After the composite modifier of 0.2 percent of Al, 0.1 percent of copper-zinc alloy and 0.13 percent of YBZW-2 alloy in the embodiment 2 is adopted, the modifier is better for refining austenite grains and eutectic carbide; the adopted heat treatment system of 650 ℃ for 5.0h → 920 ℃ for 2h → 950 ℃ for 8h → discharged air cooling can fully exert microalloying to increase secondary carbide precipitation, increase the martensite content of the strip and improve the macro hardness and the matrix micro hardness of the material. Therefore, the composite modifier scheme and the micro-alloying-austenitizing heat treatment schedule of preferred embodiment 2 of the present invention.
Example 3
The GX15 material produced by the method of example 1 was subjected to abrasion testing on a wear tester:
abrasion tester type: MSH-120;
revolution number: 2790 rpm;
abrasion of the sample: a standard abrasion tester abrades the disc;
medium: quartz sand with a particle size of 20-40 and a mixing ratio of 40% (2kg sand: 3kg water);
abrasion test time: and 8 h.
The test results are shown in Table 1.
TABLE 1 comparison of GX15 with A05 abrasion test results
As can be seen from Table 1, the abrasion ratio of GX15 was 0.605%, which was lower than the abrasion ratio of A05, which was 0.678%, and the abrasion ratio coefficient was 0.89. The abrasion resistance of the GX15 material is higher than that of the a05 material, since a smaller abrasion rate coefficient indicates a higher abrasion resistance.
The impeller and the rear guard plate in the impurity pump flow passage part are made of the GX15 material prepared by the method of example 1, and the impeller and the rear guard plate in the impurity pump flow passage part are made of the A05 material, and the results of the field abrasion test are carried out on the two materials:
the service lives of the impeller and the rear guard plate made of the A05 material are 6 months, and the service life of the impeller made of the GX15 material is about 9 months; the service life of GX15 is 1.5 times that of a05, which is a high chromium cast iron that is a popular and surpasses Cr15Mo3 developed by the crimaxmolybdenum industry corporation.
The embodiments in the present description are described in a progressive manner, each embodiment focuses on differences from other embodiments, and the same and similar parts among the embodiments are referred to each other. The device disclosed by the embodiment corresponds to the method disclosed by the embodiment, so that the description is simple, and the relevant points can be referred to the method part for description.
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (3)
1. A method for improving the wear resistance of high-chromium cast iron alloy by adopting microalloying engineering is characterized by comprising the following steps:
(1) weighing raw materials according to the chemical component proportion requirement, placing the raw materials in an induction furnace, heating until the raw materials are completely melted, and removing impurities to obtain molten iron;
(2) mixing aluminum, copper-zinc alloy and rare earth alloy as an alterant;
(3) adding the alterant in the step (2) into a casting ladle, pouring the molten iron in the step (1) into the casting ladle, stirring and slagging, and preparing for casting, wherein the casting temperature is controlled at 1380-1410 ℃;
(4) carrying out segmented heat preservation treatment on the poured material for 13-15 h;
preparing raw materials according to chemical components required by BTMCr15 in the chemical component proportion of the molten iron in the step (1), wherein the molten iron comprises the following components of 2.7-2.9 wt% of C, 0.4-0.7 wt% of Si, 2.4-3.0 wt% of Mn, 15-18 wt% of Cr, 0.9-1.1% of Cu, less than 0.06wt% of S, less than 0.10wt% of P, 0.07wt% of B and the balance of Fe;
in the step (2), molten iron is used as a measuring reference, 0.1-0.25 wt% of aluminum and 1.0wt% of copper-zinc alloy are added, and the added rare earth alloy is a mixture of 0.4wt% of YBZW-4 alloy and 0.2wt% of No. 2 rare earth silicon-iron alloy or 0.13-0.18 wt% of YBZW-2 alloy;
the segmented heat preservation and treatment process in the step (4) comprises the following steps: keeping the temperature at 650 ℃ for 5h, then heating to 920 ℃ and keeping the temperature for 2h, and finally heating to 950 ℃ and keeping the temperature for 8-10 h;
the copper and zinc alloy contains 87wt% of copper and 13wt% of zinc.
2. A high chromium alloy as claimed in claim 1 obtained by the process of microalloying to improve the wear resistance of high chromium cast iron alloy.
3. Use of the high chromium alloy according to claim 2 in the manufacture of anti-fretting iron castings.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SU1046316A1 (en) * | 1981-06-17 | 1983-10-07 | Березниковский филиал Всесоюзного научно-исследовательского и проектного института титана | Modifier for cast iron |
| CN1718816A (en) * | 2005-07-29 | 2006-01-11 | 龙南县龙钇重稀土材料有限责任公司 | Yttrium base rare earth silicon calcium iron alloy, its preparation method and use |
| CN102134674A (en) * | 2011-03-01 | 2011-07-27 | 北京工业大学 | Method for producing wear-resistant high chromium white cast iron |
| CN102330016A (en) * | 2011-09-16 | 2012-01-25 | 昆明市宜良化工设备铸造厂 | Hypoeutectic high-chromium white cast iron and preparation method thereof |
| CN103981431A (en) * | 2014-05-12 | 2014-08-13 | 安徽省宁国市亚晨碾磨铸件有限责任公司 | Wear-resistant alloy |
| CN107058856A (en) * | 2017-01-24 | 2017-08-18 | 河北高新泵业有限公司 | A kind of liquid phase alterant and the method for preparing rich chromium cast iron |
-
2020
- 2020-04-29 CN CN202010356927.4A patent/CN111424205B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SU1046316A1 (en) * | 1981-06-17 | 1983-10-07 | Березниковский филиал Всесоюзного научно-исследовательского и проектного института титана | Modifier for cast iron |
| CN1718816A (en) * | 2005-07-29 | 2006-01-11 | 龙南县龙钇重稀土材料有限责任公司 | Yttrium base rare earth silicon calcium iron alloy, its preparation method and use |
| CN102134674A (en) * | 2011-03-01 | 2011-07-27 | 北京工业大学 | Method for producing wear-resistant high chromium white cast iron |
| CN102330016A (en) * | 2011-09-16 | 2012-01-25 | 昆明市宜良化工设备铸造厂 | Hypoeutectic high-chromium white cast iron and preparation method thereof |
| CN103981431A (en) * | 2014-05-12 | 2014-08-13 | 安徽省宁国市亚晨碾磨铸件有限责任公司 | Wear-resistant alloy |
| CN107058856A (en) * | 2017-01-24 | 2017-08-18 | 河北高新泵业有限公司 | A kind of liquid phase alterant and the method for preparing rich chromium cast iron |
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