CN112981262A - Mn-containing high-boron wear-resistant alloy and preparation method thereof - Google Patents
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0006—Adding metallic additives
-
- 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
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/06—Deoxidising, e.g. killing
-
- 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
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/064—Dephosphorising; Desulfurising
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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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
- C21D1/34—Methods of heating
- C21D1/44—Methods of heating in heat-treatment baths
- C21D1/46—Salt baths
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- 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
- C22C33/06—Making ferrous alloys by melting using master alloys
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
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- 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
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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Abstract
The invention relates to a Mn-containing high-boron wear-resistant alloy and a preparation method thereof. The technical scheme is that the Mn-containing high-boron wear-resistant alloy comprises the following chemical components in percentage by weight: 0.4 to 0.5 wt% of C, 1.5 to 2.5 wt% of B, 0.7 to 0.9 wt% of Al, 0.9 to 1.5 wt% of Si, 0.02 to 0.06 wt% of Nb, 0.04 to 0.06 wt% of V, 0.25 to 0.4 wt% of Ti, 1.8 to 4.8 wt% of Mn, less than or equal to 0.06 wt% of S, less than or equal to 0.06 wt% of P, and the balance of Fe and inevitable impurities. The preparation method comprises a smelting process and a partition heat treatment process; the smelting process mainly comprises the steps of smelting and modification treatment of all components, and Mn-containing high-boron castings are obtained after smelting; the partition heat treatment process consists of austenitizing, quenching and partitioning of Mn-containing high-boron castings. The invention has low production cost, and the prepared Mn-containing high-boron wear-resistant alloy has obvious net breaking of boride, high content of retained austenite and good wear resistance and impact toughness.
Description
Technical Field
The invention belongs to the technical field of high-boron wear-resistant alloy. In particular to Mn-containing high-boron wear-resistant alloy and a preparation method thereof.
Background
With the development of economy, wear-resistant workpieces applied to engineering, mining and metallurgical machinery face increasingly severe working conditions and higher durability requirements, soThe materials for preparing the related workpieces have strong wear resistance and high toughness, and can resist wear and bear larger impact load. Compared with the common wear-resistant material, the iron-based wear-resistant alloy taking boron as the main alloy element has the advantages of low content of noble metal elements and simple production process. The hardness of boride in the alloy is high, such as FeB (1800-2000 HV) and Fe2B (1400-1800 HV) as a wear-resistant phase can improve the wear resistance of the material. But due to Fe2B-B bond in B [002]The crystals are less oriented and therefore more brittle. In addition, boride in an alloy solidification structure is continuously distributed on a three-dimensional form, the two-dimensional form is usually a fishbone shape and a net shape, and the boride in the form can seriously damage the continuity of a matrix, so that the toughness of the alloy is reduced, and the application of the high-boron wear-resistant alloy is influenced. In order to improve the toughness of the high-boron alloy, a large amount of research is carried out by domestic and foreign scholars.
"a manufacturing method of high-boron alloy with high strength and high impact toughness" (SUl,447,926) patent technology, the main chemical components of which are: 0.2-0.5% of C, 2.1-3.5% of B, 0.15-0.6% of Si, 0.25-0.8% of Mn and 0.2-0.8% of Sb, and the alloy has high boron content, has more borides in the structure and is not beneficial to improving the toughness; and the added antimony element has high content, which increases the production cost of the high boron alloy.
The patent technology of 'high-boron, high-chromium, low-carbon and wear-resistant alloy steel and a preparation method thereof' (CN101660097B) comprises the following chemical components in percentage by mass: 0.10 to 0.5% of C, 3 to 26% of Cr, 0.5 to 1.2% of Si, 0.5 to 1.5% of Mn, 0.3 to 2.8% of B, 0.3 to 2.6% of Cu, 0.2 to 0.6% of Ti, 0.02 to 0.15% of Ca, 0.03 to 0.25% of Ce, 0.02 to 0.18% of N, 0.05 to 0.3% of Nb, 0.04 to 0.09% of Al, 0.02 to 0.15% of Mg, 0.04 to 0.13% of K, less than 0.03% of S, less than 0.04% of P, and the balance of Fe and unavoidable impurity elements. The high-boron, high-chromium and low-carbon wear-resistant alloy steel has high toughness and wear resistance, does not contain noble metal elements such as Ni and Mo and the like, is low in cost, but still has insufficient toughness under the condition of high impact stress.
"a boron-containing wear-resisting alloy steel and its preparation method" (CN108220817A) patent technology, the chemical composition and its quality percentage of boron-containing wear-resisting alloy steel are: 0.6 to 0.9% of C, 5 to 5.8% of Cr, 0.5 to 1.4% of B, 0.5 to 0.8% of Ni, 0.6 to 1.0% of Mn, 0.6 to 1.0% of Si, 0.35 to 0.5% of Nb, 1.0 to 2.0% of W, 0.55 to 0.75% of Ti, less than or equal to 0.03% of S, less than or equal to 0.03% of P, and the balance of Fe and inevitable impurity elements. The boron-containing wear-resistant alloy steel is prepared by a composite method of modification treatment and mechanical treatment, so that crystal grains are refined, impact toughness is improved, and production cost is reduced. However, the alloy steel not only has higher carbon content, but also has insufficient toughness and is difficult to be applied to the working condition of high impact wear; in addition, the preparation method of the boron-containing wear-resistant alloy focuses on improving the appearance and distribution of boride, and does not provide improvement on the toughness of a matrix.
Disclosure of Invention
The invention aims to solve the problems and aims to provide a Mn-containing high-boron wear-resistant alloy with low production cost and good wear resistance and impact toughness and a preparation method thereof.
In order to achieve the purpose, the invention adopts the technical scheme that:
for the sake of simple description, the Mn-containing high-boron wear-resistant alloy is referred to as a wear-resistant alloy for short.
The wear-resistant alloy comprises the following chemical components in percentage by weight: c is 0.4-0.5 wt%; b is 1.5-2.5 wt%; 0.7-0.9 wt% of Al; si is 0.9-1.5 wt%; nb is 0.02-0.06 wt%; v is 0.04-0.06 wt%; ti is 0.25-0.4 wt%; mn is 1.8-4.8 wt%; s is less than or equal to 0.06 wt%; p is less than or equal to 0.06wt percent; the balance of Fe and inevitable impurities.
The preparation method of the wear-resistant alloy consists of a smelting process and a partition heat treatment process.
The smelting process comprises the following steps:
1) heating and smelting pig iron and scrap steel, adding a slagging medium after melting down, and carrying out primary deslagging to obtain primary deslagging alloy liquid; adding ferromanganese, ferroniobium and ferrosilicon into the primary deslagging alloy liquid according to the C, Mn and Nb content in the wear-resistant alloy, and smelting again; adding a desulfurizing agent for desulfurization after the melting down, and then carrying out secondary deslagging to obtain secondary deslagging alloy liquid.
2) Deoxidizing and fixing nitrogen in the secondary deslagging alloy liquid by using an aluminum wire, and then adding a ferrovanadium alloy and a ferrotitanium alloy into the alloy liquid subjected to deoxidization and nitrogen fixation according to the content of V and Al in the wear-resistant alloy for smelting; and adding ferroboron after melting down to enable the content of B to meet the requirement of the wear-resistant alloy, and smelting the ferroboron for 3-8 minutes to obtain the high-boron alloy liquid.
The smelting temperature in the smelting processes 1) and 2) is 1500-1550 ℃.
3) Adding a ferrosilicon inoculant accounting for 1.0-1.5 wt% of the high-boron alloy liquid and a ferrotitanium modifier accounting for 1.0-1.8 wt% of the high-boron alloy liquid into the high-boron alloy liquid, controlling the furnace temperature to be 1520-1550 ℃, and performing inoculation and primary modification treatment on the high-boron alloy liquid to enable the contents of Si and Ti in the high-boron alloy liquid to meet the requirements of the wear-resistant alloy, thereby obtaining the alloy liquid after the inoculation and the primary modification treatment.
4) And pouring the alloy liquid after the inoculation treatment and the primary modification treatment into a casting ladle, performing secondary modification treatment by adopting a pouring method, and performing air cooling to obtain a Mn-containing high-boron casting.
The modifier adopted in the second modification treatment is a mixture consisting of 0.04-0.06 wt% of rare earth magnesium alloy and 0.002-0.004 wt% of rare earth in the alloy liquid after the inoculation treatment and the primary modification treatment; the rare earth magnesium alloy and the rare earth are respectively dried for 1-1.5 hours at the temperature of 200-210 ℃ before being mixed, and are placed at the bottom of a casting ladle in advance after being mixed.
The distribution heat treatment process comprises the following steps: austenitizing the Mn-containing high-boron casting at the austenitizing temperature of 1000-1100 ℃ for 1.5-3 h to promote the fracture of a boride network structure formed in the solidification process; quenching the steel plate in a low-temperature salt bath furnace to 140-200 ℃, and keeping the temperature for 100-200 s to promote the formation of quenched martensite and residual austenite; and then placing the steel plate in a high-temperature salt bath furnace, and distributing carbon under the conditions that the temperature is 350-410 ℃ and the heat preservation time is 40-80 s, so that carbon atoms are promoted to be fully diffused from martensite to residual austenite, and the stability of the residual austenite is improved. And finally, cooling the mixture to room temperature by water to prepare the Mn-containing high-boron wear-resistant alloy.
For the purposes of the present invention, the morphology and matrix structure of the hard phase are decisive factors for the performance of Mn-containing high-boron wear-resistant alloys, and the chemical composition has an extremely important influence on these factors:
c is a solid-solution strengthening element, and can improve the strength of the steel. When the alloy is subjected to cutting wear, the increase in carbon content increases the hardness of the alloy, thereby improving the wear resistance. In addition, in the partition heat treatment process, carbon is used as a stable austenite element, so that the curve of C can be shifted to the right, the Ms point of the alloy is obviously reduced, and the stability of the retained austenite is improved. However, too high a carbon content leads to coarse acicular martensite in the matrix, increasing the brittleness of the material. Considering the integral hardness and toughness of the wear-resistant alloy, the carbon content is controlled to be 0.4-0.5 wt%.
B forms FeB or Fe with Fe2B and other borides, and the borides have higher hardness and good thermal stability. Boron can be partially dissolved in the matrix of the alloy, thereby increasing the hardenability and hardenability of the alloy. Because the content of the boron element directly determines the amount of boride in the alloy, if the content is too small, the wear resistance of the alloy is deteriorated, and if the content is too large, the boride is segregated in a grain boundary, so that the impact toughness of the alloy is influenced. Therefore, the boron content is controlled to be 1.0 to 3.0 wt%. Meanwhile, B is a cheap alloy element, and the cost of the wear-resistant alloy can be reduced by adopting boron to replace the alloy elements such as molybdenum, nickel and the like.
Nb, V and Ti can improve the hardenability of the wear-resistant alloy, and serve as heterogeneous nucleation cores in the solidification process of the alloy liquid, so that the dendritic segregation of the alloy is reduced, and the mesh distribution of boride is weakened. The invention contains titanium element, and the added ferrotitanium alterant also contains a certain titanium element, so as to improve the quantity of TiC precipitated in the solidification process of alloy liquid, thereby preventing the net growth of boride and refining austenite dendrite. Considering that the addition of excessive microalloy elements not only increases the production cost, but also causes the deterioration of the fluidity of alloy liquid and the adhesion abrasion of the prepared alloy, the content of the microalloy elements Nb is controlled to be 0.02-0.06 wt%, V is controlled to be 0.04-0.06 wt% and Ti is controlled to be 0.25-0.4 wt%.
Al and Si are used as ferrite forming elements, so that the formation of cementite in the distribution process can be effectively inhibited or delayed, carbon atoms can be fully diffused into the retained austenite from martensite without being precipitated in the form of carbide, and the stability of the retained austenite is improved. Meanwhile, considering that boron is active in property and is easy to react with nitrogen and oxygen in the smelting process, a certain amount of aluminum is added to perform nitrogen determination and oxygen removal, so that the yield of the boron is improved. However, excessive amounts of aluminum and silicon lead to an increased tendency to graphitization of the steel, and excessive amounts of silicon tend to cause decarburization of the cast product during subsequent heat treatment, which leads to poor toughness. Therefore, Al is controlled to be 0.6 to 0.9 wt% and Si is controlled to be 0.9 to 1.5 wt%.
Mn is used as an element for expanding an austenite region, can stabilize austenite, improve the hardenability of the wear-resistant alloy, reduce the Ms point of the wear-resistant alloy and increase the content of retained austenite in the wear-resistant alloy. The method fully exerts manganese element to increase the content of residual austenite in the wear-resistant alloy so as to improve the impact toughness of the wear-resistant alloy, simultaneously avoids the temper brittleness and overheating sensitivity of the wear-resistant alloy caused by excessive manganese, and controls the Mn content to be 1.8-4.3 wt%.
Due to the adoption of the technical scheme, compared with the prior art, the invention has the following positive effects:
the Mn-containing high-boron wear-resistant alloy prepared by the invention adopts a ferrosilicon inoculant accounting for 1.0-2.0 wt% of high-boron alloy liquid and a ferrotitanium modifier accounting for 1.0-3.0 wt% of high-boron alloy liquid to perform inoculation treatment and primary modification treatment. The modifier is a mixture consisting of 0.04-0.06 wt% of rare earth magnesium alloy and 0.002-0.004 wt% of rare earth in the alloy liquid after the inoculation treatment and the primary modification treatment, and the alloy liquid is subjected to secondary modification treatment by a flushing method, so that the crystal grains of the as-cast structure are refined, the mechanical property of the Mn-containing high-boron casting is improved, and the impact toughness of the wear-resistant alloy is improved.
The rare earth has a certain deoxidation and desulfurization effect, which is beneficial to removing rare earth sulfide, rare earth oxide and rare earth oxysulfide generated in the alloy liquid, and the rare earth elements can also appear on the surface of preferential growth of boride to form an adsorption film, thereby being beneficial to netCracking and spheroidizing of the boride. The invention combines the austenitizing in the partition heat treatment process to promote the fracture and the cluster spheroidization of the original reticular boride, so that the clustered boride is distributed on the matrix in an isolated and uniform way. Quenching in a low-temperature salt bath furnace in a distributed heat treatment process promotes the formation of quenched martensite and retained austenite. According to the invention, a certain amount of Mn element is added in the smelting process and the distribution in the heat treatment process is distributed, so that the residual austenite with TRIP effect in the Mn-containing high-boron wear-resistant alloy is increased, and the content of the residual austenite reaches more than 15%. The improvement of boride form and the high content of retained austenite enable the impact toughness of the Mn-containing high-boron wear-resistant alloy to reach 6.5-7.8J/cm2The improvement is nearly 200 percent compared with that before the partition heat treatment. Under the condition of sliding wear, the close combination of the spherical boride and the matrix ensures that the boride is not easy to peel off in the wear process, and the retained austenite in the matrix induces martensite phase transformation under the action of deformation, so that the hardness of the Mn-containing high-boron wear-resistant alloy is greatly improved and the Mn-containing high-boron wear-resistant alloy has good wear resistance.
The wear-resistant alloy prepared by the invention can be smelted by a common electric furnace, and the salt bath furnace is adopted for distribution heat treatment, so that the production process is simple and convenient. The prepared wear-resistant alloy has good fluidity and casting formability, can be formed by methods such as common sand casting, lost foam casting, metal mold casting, lost wax precision casting, resin sand casting, centrifugal composite casting and the like, a casting is not easy to be stained with sand, a casting head is easy to clean, and products in various shapes can be directly cast.
Therefore, the invention has low production cost, and the prepared Mn-containing high-boron wear-resistant alloy has the characteristics of good wear resistance and impact toughness
Drawings
FIG. 1 is a metallographic structure of a Mn-containing high-boron casting prepared according to the present invention;
FIG. 2 is a metallographic structure of the Mn-containing high boron casting shown in FIG. 1 after partition heat treatment;
FIG. 3 is a transmission morphology of retained austenite in the structure of the Mn-containing high boron casting shown in FIG. 1 after partition heat treatment;
FIG. 4 is a metallographic representation of the metallographic structure of another Mn-containing high boron casting made in accordance with the invention;
FIG. 5 is a metallographic structure of the Mn-containing high boron casting shown in FIG. 4 after partition heat treatment;
FIG. 6 is a transmission morphology of retained austenite in the structure of the Mn-containing high boron casting shown in FIG. 4 after partition heat treatment;
FIG. 7 is a graph of the wear surface topography of the Mn-containing high boron casting of FIG. 1;
FIG. 8 is a graph of the wear surface topography of the Mn-containing high boron casting of FIG. 1 after a portioning heat treatment;
FIG. 9 is a wear surface topography of the Mn-containing high boron casting of FIG. 4;
FIG. 10 is a graph of the wear surface topography of the Mn-containing high boron casting of FIG. 4 after a portioning heat treatment.
Detailed Description
The invention is further described with reference to the following figures and detailed description, without limiting its scope.
A Mn-containing high-boron wear-resistant alloy and a preparation method thereof. The preparation method of the embodiment comprises the following steps:
for the sake of simple description, the Mn-containing high-boron wear-resistant alloy is referred to as a wear-resistant alloy for short.
The wear-resistant alloy comprises the following chemical components in percentage by weight: c is 0.4-0.5 wt%; b is 1.5-2.5 wt%; 0.7-0.9 wt% of Al; si is 0.9-1.5 wt%; nb is 0.02-0.06 wt%; v is 0.04-0.06 wt%; ti is 0.25-0.4 wt%; mn is 1.8-4.8 wt%; s is less than or equal to 0.06 wt%; p is less than or equal to 0.06wt percent; the balance of Fe and inevitable impurities.
The preparation method of the wear-resistant alloy consists of a smelting process and a partition heat treatment process.
The smelting process comprises the following steps:
1) heating and smelting pig iron and scrap steel, adding a slagging medium after melting down, and carrying out primary deslagging to obtain primary deslagging alloy liquid; adding ferromanganese, ferroniobium and ferrosilicon into the primary deslagging alloy liquid according to the C, Mn and Nb content in the wear-resistant alloy, and smelting again; adding a desulfurizing agent for desulfurization after the melting down, and then carrying out secondary deslagging to obtain secondary deslagging alloy liquid.
2) Deoxidizing and fixing nitrogen in the secondary deslagging alloy liquid by using an aluminum wire, and then adding a ferrovanadium alloy and a ferrotitanium alloy into the alloy liquid subjected to deoxidization and nitrogen fixation according to the content of V and Al in the wear-resistant alloy for smelting; and adding ferroboron after melting down to enable the content of B to meet the requirement of the wear-resistant alloy, and smelting the ferroboron for 3-8 minutes to obtain the high-boron alloy liquid.
The smelting temperature in the smelting processes 1) and 2) is 1500-1550 ℃.
3) Adding a ferrosilicon inoculant accounting for 1.0-1.5 wt% of the high-boron alloy liquid and a ferrotitanium modifier accounting for 1.0-1.8 wt% of the high-boron alloy liquid into the high-boron alloy liquid, controlling the furnace temperature to be 1520-1550 ℃, and performing inoculation and primary modification treatment on the high-boron alloy liquid to enable the contents of Si and Ti in the high-boron alloy liquid to meet the requirements of the wear-resistant alloy, thereby obtaining the alloy liquid after the inoculation and the primary modification treatment.
4) And pouring the alloy liquid after the inoculation treatment and the primary modification treatment into a casting ladle, performing secondary modification treatment by adopting a pouring method, and performing air cooling to obtain a Mn-containing high-boron casting.
The modifier adopted in the second modification treatment is a mixture consisting of 0.04-0.06 wt% of rare earth magnesium alloy and 0.002-0.004 wt% of rare earth in the alloy liquid after the inoculation treatment and the primary modification treatment; the rare earth magnesium alloy and the rare earth are respectively dried for 1-1.5 hours at the temperature of 200-210 ℃ before being mixed, and are placed at the bottom of a casting ladle in advance after being mixed.
The distribution heat treatment process comprises the following steps: austenitizing the Mn-containing high-boron casting at 1000-1100 ℃ for 1.5-3 h to promote the fracture of a boride network structure formed in the solidification process; quenching the steel plate in a low-temperature salt bath furnace to 140-200 ℃ for 100-200 seconds to promote the formation of quenched martensite and residual austenite; and then placing the steel plate in a high-temperature salt bath furnace, and distributing carbon under the conditions that the temperature is 350-410 ℃ and the heat preservation time is 40-80 s so as to promote carbon atoms to be fully diffused from martensite to residual austenite and increase the stability of the residual austenite. And finally, cooling the mixture to room temperature by water to prepare the Mn-containing high-boron wear-resistant alloy.
Example 1
A Mn-containing high-boron wear-resistant alloy and a preparation method thereof. The preparation method in this example is:
for the sake of simple description, the Mn-containing high-boron wear-resistant alloy is referred to as a wear-resistant alloy for short.
The wear-resistant alloy comprises the following chemical components in percentage by weight: c is 0.4 wt%; b is 2.5 wt%; al is 0.88 wt%; si is 1.4 wt%; nb is 0.02 wt%; v is 0.04 wt%; ti is 0.26 wt%; mn is 1.9 wt%; s is 0.04 wt%; p is 0.05 wt%; the balance of Fe and inevitable impurities.
The preparation method of the wear-resistant alloy consists of a smelting process and a partition heat treatment process.
The smelting process comprises the following steps:
1) heating and smelting pig iron and scrap steel, adding a slagging medium after melting down, and carrying out primary deslagging to obtain primary deslagging alloy liquid; adding ferromanganese, ferroniobium and ferrosilicon into the primary deslagging alloy liquid according to the C, Mn and Nb content in the wear-resistant alloy, and smelting again; adding a desulfurizing agent for desulfurization after the melting down, and then carrying out secondary deslagging to obtain secondary deslagging alloy liquid.
2) Deoxidizing and fixing nitrogen in the secondary deslagging alloy liquid by using an aluminum wire, and then adding a ferrovanadium alloy and a ferrotitanium alloy into the alloy liquid subjected to deoxidization and nitrogen fixation according to the content of V and Al in the wear-resistant alloy for smelting; and adding ferroboron after melting down to ensure that the content of B meets the requirement of the wear-resistant alloy, and smelting the ferroboron for 4 minutes to obtain the high-boron alloy liquid.
The melting temperature in the melting processes 1) and 2) was 1500 ℃.
3) And adding a ferrosilicon inoculant accounting for 1.0 wt% of the high-boron alloy liquid and a ferrotitanium modifier accounting for 1.0 wt% of the high-boron alloy liquid into the high-boron alloy liquid, controlling the furnace temperature to be 1520-1550 ℃, and performing inoculation treatment and primary modification treatment on the high-boron alloy liquid to enable the contents of Si and Ti in the high-boron alloy liquid to meet the requirements of the wear-resistant alloy, thereby obtaining the alloy liquid after inoculation and primary modification treatment.
4) And pouring the alloy liquid after the inoculation treatment and the primary modification treatment into a casting ladle, performing secondary modification treatment by adopting a pouring method, and performing air cooling to obtain a Mn-containing high-boron casting.
The modifier adopted by the second modification treatment is a mixture consisting of 0.04 wt% of rare earth magnesium alloy and 0.002 wt% of rare earth in the alloy liquid after the inoculation treatment and the primary modification treatment; the rare earth magnesium alloy and the rare earth are respectively dried for 1 hour at the temperature of 200 ℃ before being mixed, and are placed at the bottom of a casting ladle in advance after being mixed.
The distribution heat treatment process comprises the following steps: austenitizing the Mn-containing high-boron casting at 1000 ℃ for 1.5h to promote the fracture of a boride network structure formed in the solidification process; then quenching the steel plate in a low-temperature salt bath furnace to 140 ℃ and keeping the temperature for 110s to promote the formation of quenched martensite and residual austenite; then placing the alloy into a high-temperature salt bath furnace, distributing carbon under the conditions that the temperature is 360 ℃ and the heat preservation time is 40s so as to promote carbon atoms to be fully diffused into the retained austenite from the martensite, increasing the stability of the retained austenite, and finally cooling the retained austenite to room temperature by water to prepare the Mn-containing high-boron wear-resistant alloy.
Specimens having dimensions of 10mm x 15mm were cut from the surface 1/4 of the abradable alloy using a wire cutter as shown in the accompanying drawings: FIG. 1 is a metallographic structure diagram of a Mn-containing high-boron casting prepared in this example; FIG. 2 is a metallographic structure of the Mn-containing high boron casting shown in FIG. 1 after partition heat treatment; FIG. 3 is a transmission morphology of retained austenite in the structure of the Mn-containing high boron casting shown in FIG. 1 after partition heat treatment. As can be seen from the comparison of FIG. 1 and FIG. 2, the boride in the prepared Mn-containing high-boron wear-resistant alloy has obvious fracture and spheroidization; as can be seen from fig. 3, the thin-film retained austenite with TRIP effect appears in the Mn-containing high-boron wear-resistant alloy, which is beneficial to improving the impact toughness and wear resistance of the wear-resistant alloy. Through detection: the rockwell hardness of the Mn-containing high boron casting shown in fig. 1 and the Mn-containing high boron wear-resistant alloy shown in fig. 2 at room temperature were 65.62HRC and 63.81HRC, respectively; the residual austenite content is 9.8 percent and 15.3 percent respectively; the impact toughness reaches 2.4J/cm respectively2And 6.5J/cm2。
Example 2
A Mn-containing high-boron wear-resistant alloy and a preparation method thereof. The preparation method in this example is:
for the sake of simple description, the Mn-containing high-boron wear-resistant alloy is referred to as a wear-resistant alloy for short.
The wear-resistant alloy comprises the following chemical components in percentage by weight: c is 0.45 wt%; b is 1.9 wt%; 0.75 wt% of Al; si is 1.2 wt%; nb is 0.04 wt%; v is 0.05 wt%; ti is 0.34 wt%; mn is 3.8 wt%; s is 0.05 wt%; p is 0.05 wt%; the balance of Fe and inevitable impurities.
The preparation method of the wear-resistant alloy consists of a smelting process and a partition heat treatment process.
The smelting process comprises the following steps:
1) heating and smelting pig iron and scrap steel, adding a slagging medium after melting down, and carrying out primary deslagging to obtain primary deslagging alloy liquid; adding ferromanganese, ferroniobium and ferrosilicon into the primary deslagging alloy liquid according to the C, Mn and Nb content in the wear-resistant alloy, and smelting again; adding a desulfurizing agent for desulfurization after the melting down, and then carrying out secondary deslagging to obtain secondary deslagging alloy liquid.
2) Deoxidizing and fixing nitrogen in the secondary deslagging alloy liquid by using an aluminum wire, and then adding a ferrovanadium alloy and a ferrotitanium alloy into the alloy liquid subjected to deoxidization and nitrogen fixation according to the content of V and Al in the wear-resistant alloy for smelting; and adding ferroboron after melting down to ensure that the content of B meets the requirement of the wear-resistant alloy, and smelting the ferroboron for 6 minutes to obtain the high-boron alloy liquid.
The melting temperature in the melting processes 1) and 2) is 1520 ℃.
3) Adding a ferrosilicon inoculant accounting for 1.2 wt% of the high-boron alloy liquid and a ferrotitanium modifier accounting for 1.3 wt% of the high-boron alloy liquid into the high-boron alloy liquid, controlling the furnace temperature to be 1540 ℃, and performing inoculation treatment and primary modification treatment on the high-boron alloy liquid to enable the contents of Si and Ti in the high-boron alloy liquid to meet the requirements of the wear-resistant alloy, thereby obtaining the alloy liquid after inoculation treatment and primary modification treatment.
4) And pouring the alloy liquid after the inoculation treatment and the primary modification treatment into a casting ladle, performing secondary modification treatment by adopting a pouring method, and performing air cooling to obtain a Mn-containing high-boron casting.
The modifier adopted by the second modification treatment is a mixture consisting of 0.05 wt% of rare earth magnesium alloy and 0.003 wt% of rare earth in the alloy liquid after the inoculation treatment and the primary modification treatment; the rare earth magnesium alloy and the rare earth are respectively dried for 1.2 hours at 205 ℃ before being mixed, and are placed at the bottom of a casting ladle in advance after being mixed.
The distribution heat treatment process comprises the following steps: austenitizing the Mn-containing high-boron casting at 1050 ℃ for 2h to promote the fracture of a boride network structure formed in the solidification process; then quenching the steel plate in a low-temperature salt bath furnace to 160 ℃, and keeping the temperature for 150s to promote the formation of quenched martensite and residual austenite; then placing the alloy into a high-temperature salt bath furnace, distributing carbon under the conditions that the temperature is 390 ℃ and the heat preservation time is 60s so as to promote carbon atoms to be fully diffused into the retained austenite from the martensite, increasing the stability of the retained austenite, and finally cooling the alloy to room temperature by water to prepare the Mn-containing high-boron wear-resistant alloy.
Specimens having dimensions of 10mm x 15mm were cut from the surface 1/4 of the abradable alloy using a wire cutter as shown in the accompanying drawings: FIG. 4 is a metallographic structure diagram of a Mn-containing high-boron casting prepared in accordance with the present example; FIG. 5 is a metallographic structure of the Mn-containing high boron casting shown in FIG. 4 after partition heat treatment; FIG. 6 is a transmission morphology of retained austenite in the structure of the Mn-containing high boron casting shown in FIG. 4 after partition heat treatment. As can be seen from the comparison of FIG. 4 and FIG. 5, the boride in the prepared Mn-containing high-boron wear-resistant alloy has obvious fracture and spheroidization; as can be seen from fig. 6, the Mn-containing high-boron wear-resistant alloy contains thin-film retained austenite having TRIP effect, which is beneficial to improving the impact toughness and wear resistance of the wear-resistant alloy. Through detection: the rockwell hardness of the Mn-containing high boron casting shown in fig. 4 and the Mn-containing high boron wear-resistant alloy shown in fig. 5 at room temperature were 62.32HRC and 61.24HRC, respectively; the residual austenite content is 11.8 percent and 16.4 percent respectively; the impact toughness reaches 3.3J/cm respectively2And 6.8J/cm2。
Example 3
A Mn-containing high-boron wear-resistant alloy and a preparation method thereof. The preparation method in this example is:
for the sake of simple description, the Mn-containing high-boron wear-resistant alloy is referred to as a wear-resistant alloy for short.
The wear-resistant alloy comprises the following chemical components in percentage by weight: c is 0.5 wt%; b is 1.6 wt%; 0.7 wt% of Al; si is 1.0 wt%; nb is 0.06 wt%; v is 0.06 wt%; ti is 0.38 wt%; mn is 4.7 wt%; s is 0.04 wt%; p is 0.05 wt%; the balance of Fe and inevitable impurities.
The preparation method of the wear-resistant alloy consists of a smelting process and a partition heat treatment process.
The smelting process comprises the following steps:
1) heating and smelting pig iron and scrap steel, adding a slagging medium after melting down, and carrying out primary deslagging to obtain primary deslagging alloy liquid; adding ferromanganese, ferroniobium and ferrosilicon into the primary deslagging alloy liquid according to the C, Mn and Nb content in the wear-resistant alloy, and smelting again; adding a desulfurizing agent for desulfurization after the melting down, and then carrying out secondary deslagging to obtain secondary deslagging alloy liquid.
2) Deoxidizing and fixing nitrogen in the secondary deslagging alloy liquid by using an aluminum wire, and then adding a ferrovanadium alloy and a ferrotitanium alloy into the alloy liquid subjected to deoxidization and nitrogen fixation according to the content of V and Al in the wear-resistant alloy for smelting; and adding ferroboron after melting down to ensure that the content of B meets the requirement of the wear-resistant alloy, and smelting the ferroboron for 8 minutes to obtain the high-boron alloy liquid.
The melting temperature in melting processes 1) and 2) was 1540 ℃.
3) And adding a ferrosilicon inoculant accounting for 1.5 wt% of the high-boron alloy liquid and a ferrotitanium modifier accounting for 1.8 wt% of the high-boron alloy liquid into the high-boron alloy liquid, controlling the furnace temperature to 1550 ℃, and performing inoculation treatment and primary modification treatment on the high-boron alloy liquid to enable the contents of Si and Ti in the high-boron alloy liquid to meet the requirements of the wear-resistant alloy, thus obtaining the alloy liquid after the inoculation treatment and the primary modification treatment.
4) And pouring the alloy liquid after the inoculation treatment and the primary modification treatment into a casting ladle, performing secondary modification treatment by adopting a pouring method, and performing air cooling to obtain a Mn-containing high-boron casting.
The modifier adopted by the second modification treatment is a mixture consisting of 0.06 wt% of rare earth magnesium alloy and 0.004 wt% of rare earth in the alloy liquid after the inoculation treatment and the primary modification treatment; the rare earth magnesium alloy and the rare earth are respectively dried for 1.5 hours at 210 ℃ before being mixed, and are placed at the bottom of a casting ladle in advance after being mixed.
The distribution heat treatment process comprises the following steps: austenitizing the Mn-containing high-boron casting at 1100 ℃ for 3h to promote the fracture of a boride network structure formed in the solidification process; then quenching the steel plate to 190 ℃ in a low-temperature salt bath furnace, and keeping the temperature for 200s to promote the formation of quenched martensite and residual austenite; then placing the alloy into a high-temperature salt bath furnace, distributing carbon under the conditions that the temperature is 410 ℃ and the heat preservation time is 75s to promote carbon atoms to be fully diffused into the retained austenite from the martensite, increasing the stability of the retained austenite, and finally cooling the alloy to room temperature by water to prepare the Mn-containing high-boron wear-resistant alloy.
The Mn-containing high-boron wear-resistant alloy prepared in the embodiment is detected as follows: the Rockwell hardness of the Mn-containing high-boron casting and the Mn-containing high-boron wear-resistant alloy at room temperature are 61.08HRC and 58.89HRC respectively; the residual austenite content is 12.5 percent and 16.9 percent respectively; the impact toughness reaches 3.8J/cm respectively2And 7.8J/cm2。
The wear test of the Mn-containing high-boron wear-resistant alloy prepared by the specific embodiment is as follows:
the abrasion test of the embodiment is carried out on an MLD-10 type testing machine, and the adopted abrasion standard sample is NM 500; the upper samples are respectively prepared Mn-containing high-boron castings and Mn-containing high-boron wear-resistant alloys, and the processing sizes are 10mm multiplied by 30 mm. The lower sample was a ring butt-ground sample of GCr15 steel. In an abrasion experiment, the rotating speed of a lower sample is 100r/min, an upper sample is abraded for 4 hours, the upper sample is weighed once every 1 hour, the upper sample is cleaned by alcohol after sampling, the abrasion loss weight is measured on a photoelectric balance with the precision of 0.1mg after hot air drying, and the abrasion loss weight is compared with the abrasion loss weight of NM500, so that the relative abrasion resistance of the upper sample is obtained: the relative wear resistance of the upper samples of the Mn-containing high boron castings of examples 1, 2 and 3 were 2.05, 1.93 and 1.88, respectively; and the relative wear resistance of the upper samples of the Mn-containing high boron wear resistant alloys of example 1, example 2 and example 3 after the partition heat treatment was 2.78, 2.69 and 2.65, respectively.
The wear surface topography of the Mn-containing high boron castings and Mn-containing high boron wear resistant alloy specimens prepared in examples 1 and 2, respectively, are shown in fig. 7-10: FIG. 7 is a graph of the wear surface topography of the Mn-containing high boron casting of FIG. 1; FIG. 8 is a graph of the wear surface topography of the Mn-containing high boron casting of FIG. 1 after a portioning heat treatment; FIG. 9 is a wear surface topography of the Mn-containing high boron casting of FIG. 4; FIG. 10 is a graph of the wear surface topography of the Mn-containing high boron casting of FIG. 4 after a portioning heat treatment. As can be seen from fig. 7 and 9: wear indicates different degrees of wear shedding; as can be seen from fig. 8 and 10, the retained austenite content having TRIP effect is increased after the partition heat treatment, and the matrix having higher impact toughness can contain boride to prevent the boride from being exfoliated.
The experimental result shows that the three Mn-containing high-boron wear-resistant alloys prepared by the invention have good mechanical properties; compared with the cast state, the forms of borides in the Mn-containing high-boron wear-resistant alloy structure obtained after the partition heat treatment are obviously broken and spheroidized, the content of residual austenite is increased, and the impact toughness and the wear resistance are improved. The Mn content of the Mn-containing high-boron wear-resistant alloy in the example 3 is higher than that of the Mn-containing high-boron wear-resistant alloy in the example 2 and the example 1, and the improvement of the impact toughness and the wear resistance is larger.
For the present embodiment, the morphology and the matrix structure of the hard phase are the determining factors for the performance of the Mn-containing high-boron wear-resistant alloy, and the chemical composition has an extremely important influence on the factors:
c is a solid-solution strengthening element, and can improve the strength of the steel. When the alloy is subjected to cutting wear, the increase in carbon content increases the hardness of the alloy, thereby improving the wear resistance. In addition, in the partition heat treatment process, carbon is used as a stable austenite element, so that the curve of C can be shifted to the right, the Ms point of the alloy is obviously reduced, and the stability of the retained austenite is improved. However, too high a carbon content leads to coarse acicular martensite in the matrix, increasing the brittleness of the material. Considering the integral hardness and toughness of the wear-resistant alloy, the carbon content is controlled to be 0.4-0.5 wt%.
B forms FeB or Fe with Fe2B and other borides, and the borides have higher hardness and good thermal stability. Boron can be partially dissolved in the matrix of the alloy, thereby increasing the hardenability and hardenability of the alloy. Because the content of boron directly determines the amount of boride in the alloy, too small content can cause the wear resistance of the alloy to be poor, and too much boron can cause the boride to be segregated in grain boundaries, thereby influencing the toughness of the alloy. Therefore, the boron content is controlled to be 1.0 to 3.0 wt%. Meanwhile, B is a cheap alloy element, and the cost of the wear-resistant alloy can be reduced by adopting boron to replace the alloy elements such as molybdenum, nickel and the like.
Nb, V and Ti can improve the hardenability of the wear-resistant alloy, and serve as heterogeneous nucleation cores in the solidification process of the alloy liquid, so that the dendritic segregation of the alloy is reduced, and the mesh distribution of boride is weakened. The titanium-iron modifier contains titanium element, and the added titanium-iron modifier also contains certain titanium element, so that the amount of TiC precipitated in the solidification process of the alloy liquid is increased, the network growth of boride is prevented, and austenite dendrite is refined. Considering that the addition of excessive microalloy elements not only increases the production cost, but also causes the deterioration of the fluidity of alloy liquid and the adhesion abrasion of the prepared alloy, the content of the microalloy elements Nb is controlled to be 0.02-0.06 wt%, V is controlled to be 0.04-0.06 wt% and Ti is controlled to be 0.25-0.4 wt%.
Al and Si are used as ferrite forming elements, so that the formation of cementite in the distribution process can be effectively inhibited or delayed, carbon atoms can be fully diffused into the retained austenite from martensite without being precipitated in the form of carbide, and the stability of the retained austenite is improved. Meanwhile, considering that boron is active in property and is easy to react with nitrogen and oxygen in the smelting process, a certain amount of aluminum is added to perform nitrogen determination and oxygen removal, so that the yield of the boron is improved. However, excessive amounts of aluminum and silicon lead to an increased tendency to graphitization of the steel, and excessive amounts of silicon tend to cause decarburization of the cast product during subsequent heat treatment, which leads to poor toughness. Therefore, Al is controlled to be 0.6 to 0.9 wt% and Si is controlled to be 0.9 to 1.5 wt%.
Mn is used as an element for expanding an austenite region, can stabilize austenite, improve the hardenability of the wear-resistant alloy, reduce the Ms point of the wear-resistant alloy and increase the content of retained austenite in the wear-resistant alloy. The specific embodiment is to give full play to manganese element to increase the content of retained austenite in the wear-resistant alloy so as to improve the toughness of the wear-resistant alloy, avoid the temper brittleness and overheating sensitivity of the wear-resistant alloy caused by excessive manganese, and control Mn to be 1.8-4.3 wt%.
Compared with the prior art, the specific implementation mode has the following positive effects:
the Mn-containing high-boron wear-resistant alloy prepared by the specific embodiment adopts a ferrosilicon inoculant accounting for 1.0-2.0 wt% of the high-boron alloy liquid and a ferrotitanium modifier accounting for 1.0-3.0 wt% of the high-boron alloy liquid to perform inoculation treatment and primary modification treatment. The modifier is a mixture consisting of 0.04-0.06 wt% of rare earth magnesium alloy and 0.002-0.004 wt% of rare earth in the alloy liquid after the inoculation treatment and the primary modification treatment, and the alloy liquid is subjected to secondary modification treatment by a flushing method, so that the crystal grains of the as-cast structure are refined, the mechanical property of the Mn-containing high-boron casting is improved, and the impact toughness of the wear-resistant alloy is improved.
The rare earth has a certain deoxidation and desulfurization effect, which is beneficial to removing rare earth sulfide, rare earth oxide and rare earth oxysulfide generated in the alloy liquid, and the rare earth elements can also appear on the surface of preferential growth of boride to form an adsorption film, thereby being beneficial to cracking and spheroidizing of the net boride. The specific embodiment combines austenitizing in the partition heat treatment process to promote the fracture and cluster spheroidization of the original reticulated boride, so that the pelletized boride is distributed on the matrix in an isolated and uniform manner. Quenching in a low-temperature salt bath furnace in a distributed heat treatment process promotes the formation of quenched martensite and retained austenite. In the specific embodiment, a certain amount of Mn element is added in the smelting process and the distribution in the heat treatment process is distributed, so that the residual austenite with the TRIP effect in the Mn-containing high-boron wear-resistant alloy is increased, and the content of the residual austenite reaches more than 15%. The improvement of boride form and the high content of retained austenite enable the impact toughness of the Mn-containing high-boron wear-resistant alloy to reach 6.5-7.8J/cm2Is less advanced thanThe improvement is nearly 200 percent before the partition heat treatment. Under the condition of sliding wear, the close combination of the spherical boride and the matrix ensures that the boride is not easy to peel off in the wear process, and the retained austenite in the matrix induces martensite phase transformation under the action of deformation, so that the hardness of the Mn-containing high-boron wear-resistant alloy is greatly improved and the Mn-containing high-boron wear-resistant alloy has good wear resistance.
The wear-resistant alloy prepared by the specific embodiment can be smelted by a common electric furnace, and is subjected to partition heat treatment by a salt bath furnace, so that the production process is simple and convenient. The prepared wear-resistant alloy has good fluidity and casting formability, can be formed by methods such as common sand casting, lost foam casting, metal mold casting, lost wax precision casting, resin sand casting, centrifugal composite casting and the like, a casting is not easy to be stained with sand, a casting head is easy to clean, and products in various shapes can be directly cast.
Therefore, the specific embodiment has low production cost, and the prepared Mn-containing high-boron wear-resistant alloy has the characteristics of good wear resistance and impact toughness.
Claims (2)
1. A preparation method of Mn-containing high-boron wear-resistant alloy is characterized by comprising the following steps: for convenience of description, the Mn-containing high-boron wear-resistant alloy is referred to as a wear-resistant alloy for short;
the wear-resistant alloy comprises the following chemical components in percentage by weight: 0.4 to 0.5 wt% of C, 1.5 to 2.5 wt% of B, 0.7 to 0.9 wt% of Al, 0.9 to 1.5 wt% of Si, 0.02 to 0.06 wt% of Nb, 0.04 to 0.06 wt% of V, 0.25 to 0.4 wt% of Ti, 1.8 to 4.8 wt% of Mn, less than or equal to 0.06 wt% of S, less than or equal to 0.06 wt% of P, and the balance of Fe and inevitable impurities;
the preparation method of the wear-resistant alloy consists of a smelting process and a partition heat treatment process;
the smelting process comprises the following steps:
1) heating and smelting pig iron and scrap steel, adding a slagging medium after melting down, and carrying out primary deslagging to obtain primary deslagging alloy liquid; adding ferromanganese, ferroniobium and ferrosilicon into the primary deslagging alloy liquid according to the C, Mn and Nb content in the wear-resistant alloy, and smelting again; adding a desulfurizing agent for desulfurization after the melting down, and then carrying out secondary deslagging to obtain secondary deslagging alloy liquid;
2) deoxidizing and fixing nitrogen in the secondary deslagging alloy liquid by using an aluminum wire, and then adding a ferrovanadium alloy and a ferrotitanium alloy into the alloy liquid subjected to deoxidization and nitrogen fixation according to the content of V and Al in the wear-resistant alloy for smelting; adding ferroboron after melting down to enable the content of B to meet the requirement of the wear-resistant alloy, and smelting the ferroboron for 3-8 minutes to obtain high-boron alloy liquid;
the smelting temperature in the smelting processes 1) and 2) is 1500-1550 ℃;
3) adding a ferrosilicon inoculant accounting for 1.0-1.5 wt% of the high-boron alloy liquid and a ferrotitanium modifier accounting for 1.0-1.8 wt% of the high-boron alloy liquid into the high-boron alloy liquid, controlling the furnace temperature to be 1520-1550 ℃, and performing inoculation treatment and preliminary modification treatment on the high-boron alloy liquid to enable the contents of Si and Ti in the high-boron alloy liquid to meet the requirements of the wear-resistant alloy, so as to obtain an alloy liquid after the inoculation treatment and the preliminary modification treatment;
4) pouring the alloy liquid after inoculation and primary modification into a casting ladle, performing secondary modification by adopting a pouring method, and performing air cooling to obtain a Mn-containing high-boron casting;
the modifier adopted in the second modification treatment is a mixture consisting of 0.04-0.06 wt% of rare earth magnesium alloy and 0.002-0.004 wt% of rare earth in the alloy liquid after the inoculation treatment and the primary modification treatment; drying the rare earth magnesium alloy and the rare earth for 1-1.5 hours at 200-210 ℃ respectively before mixing, and placing the mixture at the bottom of a casting ladle in advance;
the distribution heat treatment process comprises the following steps: austenitizing the Mn-containing high-boron casting at the austenitizing temperature of 1000-1100 ℃ for 1.5-3 h; quenching the steel plate in a low-temperature salt bath furnace to 140-200 ℃, and keeping the temperature for 100-200 s; and then placing the alloy in a high-temperature salt bath furnace, carrying out carbon distribution under the conditions that the temperature is 350-410 ℃ and the heat preservation time is 40-80 s, and finally cooling the alloy to room temperature by water to obtain the Mn-containing high-boron wear-resistant alloy.
2. A Mn-containing high-boron wear-resistant alloy, characterized in that the Mn-containing high-boron wear-resistant alloy is a Mn-containing high-boron wear-resistant alloy prepared according to the method for preparing a Mn-containing high-boron wear-resistant alloy of claim 1.
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