KR20190030480A - Wheel blade having a high hardness and anti-wearness, and making method there-of, and Die for making a wheel blade - Google Patents

Abstract

The present invention relates to a wheel blade assembled to and used for a shot blasting apparatus which shots a shot (steel) ball with a size of 0.2 to 2 mm on a surface of a steel plate as a pretreatment process, such as descaling, plating, and coating for a steel plate, or to remove sand, slag, and foreign substances stuck on a surface of a casting and, more specifically, to a wheel blade of a shot blasting apparatus with high hardness and high abrasion resistance, and a method and a die for manufacturing the same. According to the present invention, the wheel blade is formed with a material comprising: 13 to 20 weight percent of Mo; 18 to 30 weight percent of Co; 3 to 6 weight percent of V; 3 to 5 weight percent of Cr; 1.5 to 3.5 weight percent of C; 0.5 to 1.2 weight percent of Si; 0.1 to 0.5 weight percent of Mn; 2.5 to 4.5 weight percent of B; 1 to 2 weight percent of Nb; 1 to 3 weight percent of W; 0.1 to 0.2 weight percent of Al; 0.1 to 0.3 weight percent of Ti; 0.1 to 0.2 weight percent of rare earth metal (RE); and the balance of Fe and inevitable impurities. Moreover, an end part of the wheel blade has a higher impact strength than that of an inner side and a bulk hardness value is 67 to 68 in HRC.

Description

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a wheel blade for a short wheel having high hardness and high abrasion resistance, a method for manufacturing the wheel blade, and a mold for manufacturing a wheel blade.

In the present invention, a shot ball or steel ball having a size of 0.5 to 2 mm is projected on the surface of a steel sheet by a pretreatment process such as de-lime of a steel sheet, plating, painting or the like, or sand or slag And more particularly to a wheel blade having a high hardness and a high wear resistance, a method for manufacturing the same and a method for manufacturing the wheel blade used for manufacturing a wheel blade. The present invention relates to a mold.

As shown in Fig. 1, there is a rotating wheel (11) assembled with eight blades (12) as a component for continuously projecting a shot ball on an object. The centrifugal force of the wheel The impact is applied to this subject with a strong force, and the deodorization and the foreign matter are removed by this impact.

The wheel blade 12 used here has a shape as shown in Fig. 2, which makes contact friction with thousands of times to several tens of thousands of times per minute, and can not withstand wear with ordinary metal alloys. The shot ball used here is a high carbon alloy steel with a hardness of HRC 45 to 55, which is very high.

The material that can withstand high-hardness steel balls and continuous friction wear is the highest wear resistant material ever used in high chromium white cast iron (Cr15 ~ 18%, Mo3%). Some makers use 27Cr2Mo white cast iron, which is less abrasive than 15Cr3Mo white cast iron.

Certain companies raise their carbon content by more than 2.5% in Tungsten high speed steel products and sell them at more than twice the price, but the wear resistance is only about 50% better than the chrome white cast iron.

Short-wheel blades that have been commercialized so far are the above-mentioned products and are being used as products of great popularity all over the world. In recent years, when the shot blasting operation is performed in an automatic line that is continuously operated for 24 hours by automation of the post-casting treatment line, the service life of the wheel blade becomes very important, and the operation efficiency and productivity of the entire line are greatly improved It was a problem. In addition, the Descaling work of the steel plate is also carried out for 24 hours continuously, which has the same problem as that of the casting plant.

The commercially available wheel blades have a service life of only one week to ten days, which results in demanding long-life products.

The wheel blades that have been used so far have not been available for more than two weeks, and those with high wheel blade usage are currently imported from abroad. In recent years, domestic manufacturers have developed new products to replace imported products, but this product could not exceed the lifespan of almost two weeks with almost the same lifetime as imports. The product developed by this company is not a product made by casting (KS-STD11) (JIS-SKD11) cold steel tool steel but it is formed by rolling or forging to a machining center. It is produced by machining and vacuum heat treatment, which is the best long life product produced domestically.

According to metallurgical data, STD11 steel is much less abrasion resistant than 15Cr3Mo white cast iron.

Nonetheless, the reason why the above-mentioned STD11-type plate machined and vacuum heat-treated products are superior in wear resistance is not a matter of material but a problem of unevenness in the texture of castings and forgings (including rolling) Or whisking, the entire surface of the structure is homogenized. Therefore, even when the heat treatment is performed, the hardness of the surface is very uniform so that the wear does not occur. On the other hand, the casting has different cooling rates depending on the position of the casting mold, This is because the organization must be uneven.

On the other hand, in the above-mentioned casting, although the amount of carbide and hardness of the carbide is high in the microscopic structure, the structure is irregular in each part and uneven wear occurs. As a result, STD11, which is an alloy tool steel for cold- Which is shorter than that produced by forging.

However, there is a problem that the product manufactured by rolling or forging is inferior in economic efficiency due to a complicated manufacturing process due to a high production cost, and the use life is about two weeks, I am not satisfied.

For reference, the chemical composition of STD11 species is 1.4 to 1.6% of C, 0.4% or less of Si, 0.6% or less of Mn, 11 to 13% of Cr, 0.8 to 1.2% of Mo, and 0.2 to 0.5% of V . The maximum hardness of this grade is about HRC65.

In order to solve this problem, the present invention has been made to solve the above problems by using a boride having a hardness higher than that of a carbide instead of chromium carbide, which is a chromium carbide which depends on existing products in terms of hardness and abrasion resistance, The present invention provides a wheel blade and a manufacturing method thereof,

Another object of the present invention is to provide a mold capable of manufacturing a wheel blade having high hardness and abrasion resistance.

In order to achieve the above object,

Wherein the molybdenum (Mo) is 13 to 20%, the cobalt (Co) is 18 to 30%, the vanadium (V) is 3 to 6%, the chromium (Cr) is 3 to 5% 0.5 to 1.2% of silicon (Si), 0.1 to 0.5% of manganese (Mn), 2.5 to 4.5% of boron (B), 1 to 2% of niobium Nb and 1 to 2% of tungsten (Fe) and inevitable impurities, and the balance being composed of iron (Fe) and unavoidable impurities, in the range of 0.1 to 3%, aluminum (Al) of 0.1 to 0.2%, titanium (Ti) of 0.1 to 0.3% Characterized in that the bulk hardness value is in the range of HRC 67 to 68, while the end portion has a higher impact strength than the inner side, and the hard hardness value and the high wear resistance are characterized by being a wheel blade for a short-

In addition, it is preferable that the steel material contains 13 to 20% of Mo, 18 to 30% of cobalt, 3 to 6% of vanadium, 3 to 5% of chromium, 3 to 5% of carbon, 1.5 to 3.5 percent silicon, 0.5 to 1.2 percent silicon, 0.1 to 0.5 percent manganese, 2.5 to 4.5 percent boron, 1 to 2 percent niobium, 1 to 2 percent tungsten, (Fe) in an amount of 1 to 3%, 0.1 to 0.2% of aluminum (Al), 0.1 to 0.3% of titanium (Ti), 0.1 to 0.2% Melting at 1650 캜 30 캜 in an induction furnace,

Injecting the melted molten metal into a mold for casting a wheel blade at 1560 占 폚 占 10 占 폚,

Cooling the metal mold into which the molten metal is injected,

Normalizing the wheel blade at 750 to 850 ° C,

Elevating the normalized wheel blade to 1050 DEG C +/- 20 DEG C, subjecting it to austenizing,

Oil quenching the austenized wheel blades,

And a pressing step of holding the oil-quenched wheel blade at 530 ° C to 580 ° C for 2 hours to 2 hours and 20 minutes, characterized by comprising a step of tempering and a method of manufacturing a wheel blade for a short wheel having high wear resistance ,

In the mold for manufacturing a blade of a vertically divided casting type comprising a casting mold for casting molten metal, an injection port for leading the casting mold to the casting mold, and a mold space of the blade product,

The sprue is largely formed so as to serve as a role of quick injection and air bubbling,

The injection port includes an upper injection port and a lower injection port,

The bottom of the sprue is formed with a concave bottom surface for suppressing the generation of vortex of the molten metal,

Characterized in that the mold space of the blade product is formed such that an inner side portion of the blade ball which is first contacted by the shot ball faces the injection port and a tip hole is formed at an end of the mold space to allow gas to escape. .

Industrial Applicability According to the present invention, it is easy to manufacture a wheel blade for a short chain having high hardness and high abrasion resistance, so that the service life of the wheel blade can be remarkably improved.

Fig. 1 is a schematic view of a wheel blade assembled and used in a short-
Fig. 2 is a perspective view of a blade mounted on a wheel,
3 is a cross-sectional view of a mold for manufacturing a wheel blade viewed from the front,
4 is a sectional view of a mold for manufacturing a wheel blade viewed from the side.

As described above, the Wheel Blade, which is a part of the Shot Blasting Machine, should be made of an alloy material which can withstand friction and wear between metals as a consumable tool. The most important factor that determines wear resistance is hardness. Hardness is divided into two types, one is the hardness of the microstructure and the other is the hardness of the matrix.

Here, the term "base structure" refers to a background structure, and microhardness refers to various intermetallic compounds that are mixed in a base structure. Typical examples are carbides, nitrides, main compounds and complex compounds. These intermetallic compounds have a very high hardness, a high melting point and a very high bonding strength. In addition, it is chemically stable and does not corrode well. Second, the bulk hardness must be high in order to have excellent abrasion resistance. Secondly, many intermetallic compounds such as carbide, nitride and boride which are microstructures must exist.

Where the matrix is austenite when the metal is in a molten state and it turns into a solid by cooling and becomes a pearlite structure. When the cooling rate becomes higher, it transforms into martensite. The martensite has the highest hardness. Even though 100% martensitic structure is not obtained in the casting state, it can be transformed into martensitic structure by heat treatment after casting.

Analyzing the structure of various materials used as wheel blades up to now, most of the base structure is made of martensite and the high hardness material of microstructure is composed of chromium carbide. Chromium carbide, such as 15Cr3Mo, 27Cr2Mo, and STD11 described above, is a microstructure material that improves abrasion resistance.

Table 1 shows the hardness of various carbides.

Vickers Hardness and Knoop Hardness    material or phase      hardness HV     knoop hardness  Pearlite (matrix)        300 to 800      300 to 600  Martensite (matrix)        500 to 900      500 to 800  Cementite (Fe3C)        840-1100      1,025  Chrome Carbide (Cr7C3)        1,200-1,600      1,735  Moly Carbide (Mo2C)        1,500 - 1,800      1,800  Tungsten Carbide (WC.W2C, W6C)        1,800-2,400      1,800  Niobium Carbide (NbC)        2,400      2,400  Silicon Carbide (SiC)        2,600      2,660  Vanadium Carbide (VC)        2,800      2,470  Titanium Carbide (TiC)        3,200      2,580  Boron Carbide (B4C)        3,700      2,800  Diamond        10,000      7,575

As shown in Table 1, the chromium carbide has a relatively low hardness value.

For the wheel blade to have the highest abrasion resistance, the bulk hardness must first be high. Bulk hardness is the composite hardness of the hardness and microhardness of the matrix and is usually expressed as Brinell hardness or Rockwell hardness. Here, Brinell hardness is used to measure the hardness of a steel with a relatively low hardness value, and Rockwell hardness is used to measure the hardness of the hardness steel.

The existing commercially available wheel blades are HRC62 to HRC64. In the case of STD11, which is the wheel blade material having the longest life described above, HRC65 is the hardness at which the maximum value can be obtained.

As mentioned above, HRC65 is the maximum hardness value obtained from materials of conventional products, and the maximum life is up to 2 weeks in continuous shot blasting machines operating 24 hours at this time. In order to overcome this limitation, it is almost impossible to use chromium carbide. In the present invention, vanadium carbide, tungsten carbide, boron carbide and boron compounds such as molybdenum boride, cobalt Cobalt Boride and Niobium Boride are mixed together in a large amount so that the minimum hardness is at least HRC67.

In the case of T15 and M4, which are generally considered to have the highest abrasion resistance among high-speed steel materials, HRC 66 to 67 are the highest hardness values.

Table 2 shows the hardness values of various borides.

The melting point and hardness (HV)       Boride     Melting Point (° C)    HV-Hardness  Aluminum Boride (AlB2)          1,350        2,000  Chrome Boride (CrB2)          1,850        2,100  Cobalt Boride (CoB)          1,400        2,000  Iron Boride (FeB)          1,390        1,800  Nickel Boride (Ni2B)          1,220        1,800  Niobium Boride (NbB)          2,270        2,700  Molybdenum Boride (MoB2)          2,000        2,300  Titanium Boride (TiB2)          3.225        3,300  Vanadium Boride (VB)          2,100        2,500  Tungsten Boride (W2B5)          2,800        3,000  Zirconium Boride (ZrB2)          3,050        2,050

The description so far has been directed to the role of contributing to the composition and abrasion resistance of the metal structure depending on the chemical composition.

Even if the chemical components are the same, the crystal grains of the metal vary in size depending on the cooling rate during casting. If the crystal grains are large, the hardness and the mechanical properties deteriorate, and if the crystal grains are fine, the impact strength and the abrasion resistance are improved as well as the hardness.

Taking all of these characteristics into consideration, it is a technical challenge to produce the best abrasion resistance products.

Ultimate Hardness To obtain the highest abrasion resistance, we designed a special high-speed steel alloy primarily to achieve Bulk hardness with Rockwell hardness of HRC67-68.

Specifically, it is preferable that the carbon (C) is 1.5 to 3.5%, the silicon (Si) is 0.5 to 1.2%, the manganese (Mn) is 0.1 to 0.5%, the chromium (Cr) is 3 to 5% 3 to 6% of vanadium (V), 18 to 30% of cobalt (Co), 1 to 2% of niobium (Nb), 1 to 3% of tungsten (W) 0.3 to 0.3% of aluminum, 0.1 to 0.2% of aluminum (Al), 0.1 to 0.2% of hydrazine metal (RE) and 2.5 to 5% of boron (B).

The properties of this high-speed steel are not high-speed steel for cutting tools requiring high-temperature hardness and strength, but are high-speed steel alloys for ultra-abrasion wear at a working temperature of less than 500 ° C. Therefore, we focused on maximizing bulk hardness and microhardness.

In the alloy design of the present invention, the carbon is alloyed to form a carbide, and its content is 1.5% to 3.5% by weight. The more effective content is 2.0% ~ 3.0%. If the content of carbon exceeds 3.5%, the ratio of boron to boron carbide increases, resulting in an increase in hardness but a stronger brittleness.

Here, silicon (Si) is a major element that improves the role of deoxidizer and castability. Generally, in high-speed steel, 0.4% or less of alloy is used, but in the present invention, 0.5 to 1.2% of alloy is used for deoxidation and improvement of castability. Preferably, 0.7 to 1.0% is more effective.

Manganese has no purpose other than deoxidizing purposes. Manganese in tool steel is helpful in increasing toughness, but it is counterproductive in increasing hardness. Therefore, it is limited to 0.1 to 0.5%. This content is also acceptable for inclusion in scrap iron or other ferroalloys.

Here, chromium (Chromium) is limited to 3-5%. This is also the level of chromium in conventional high speed steels. As shown in Table 1, chromium carbide has a relatively low hardness of about HV1,300. In addition, since chromium easily forms carbide, if the chromium content is exceeded, the carbide of other elements having high hardness becomes small, and the bulk hardness becomes low.

Here, vanadium (V) serves to increase the microhardness by forming an MC type carbide. In addition, it plays a role of miniaturizing the size of crystal grains and alloys 3 to 6% by weight. In high speed steel where boron is not included, vanadium is a key element for increasing wear resistance, and when boron is alloyed, the bulk hardness is lowered and 3 ~ 6% shows good results.

Here, Niobium is an element that forms a typical MC type carbide together with vanadium. As shown in Table 1, the hardness of HV2400 is very high. However, since niobium tends to coarsen crystal grains, it is limited to 1 to 2% in the present invention.

Tungsten, like molybdenum, is an element that forms carbide and boride. It plays a role in increasing micro hardness and abrasion. However, when the price is high and molybdenum content is high, it is not necessary to increase the tungsten content. , And the weight of the product is limited to 1 to 3% by weight in order to increase the weight of the product.

Here, molybdenum is the most important element with cobalt. Although molybdenum forms carbide, it does not have a high tendency to form carbides such as chromium or tungsten vanadium, and also forms carbide of M2C type. Therefore, hardness of carbide is comparatively low as HV1,800. However, boron and boride are easily boride, and the hardness of molyboryide is HV2,000 as shown in Table 2. In addition, in the present invention, molybdenum is alloyed in an amount of 13 to 20% by weight. The amount of molybdenum is required to be increased or decreased according to the content of boron. Since the present invention is a wheel blade, heat resistance, high temperature strength, higher hardness and abrasion resistance are more important. A preferred content of 15 to 18% is most effective for these properties.

Here, Cobalt forms a cobalt boride by bonding with boron. In Table 2, the CoB has a very low Melting Point of 1,400 ° C. and easily forms boride. Nevertheless, the hardness of CoB Very high at HV2,000. Therefore, in the present invention, the content of cobalt is limited to a minimum of 18% and a maximum of 30% by weight. More preferably 20 to 25%. Since cobalt is the most expensive element among the alloys required for the present invention, it is uneconomical because the cost of the alloy increases when the content is increased.

Here, boron is a key element in addition to molybdenum and cobalt. Boron has very similar properties to carbon. Boron has atomic number 5, atomic weight is 10.82, carbon is atomic number 6, and atomic number is 12. Like carbon, it reacts easily with iron (Fe). The temperature of the process point of iron and carbon is low at 1,134 ℃ and the temperature of process point of iron and boron is low at 1,179 ℃. Boron forms boride just as carbon makes carbide. Both materials are intermetallic compounds. Unusual is that boride is harder than carbide. By using the properties of boron, the content of boron is limited to 1.5 to 5% by weight in the present invention. The content of boron is limited to not less than 1.5%. In this case, the hardness is lowered and the effect is less in the present invention. When the boron content is more than 5%, the brittleness is strong.

Titanium is used as a deoxidizing agent and grain refinement element in a weight ratio of 0.1 to 0.2%, and when it exceeds 0.2%, the cast hardness is lowered.

Aluminum is used as a deoxidizer and 0.1 ~ 0.2% is effective. Aluminum also forms aluminum boride at low temperatures, as shown in Table 2, and its hardness is also very high. When the aluminum is too high, the impact strength is lowered, so 0.1 to 0.2% is suitable.

Here, rare earth metals (Rare Earth Metal) are used for deoxidation and desulfurization purposes and 0.1 to 0.2% are effective. When using rare earth elements, the impact strength is higher than when they are not used. This is because the rare earth element has a desulfurizing effect to remove sulfur, and is particularly advantageous in terms of high temperature strength.

In the blade according to the present invention, the end on which the short ball contacts first, that is, the end on the wide side of the product, that is, the side on which the shot ball is projected is higher in hardness than the inner side, 68,

The reason for this is that the projection of the shot ball causes high-speed friction, and if the hardness is less than HRC 66, the abrasion occurs easily. Existing shot wheel blades could not exceed HRC65 and could not be replaced for more than 2 weeks.

In addition, in the present invention, a technical problem as important as an alloy design is a casting method, and even if a suitable alloy design is not appropriate, the desired purpose can not be achieved unless the casting method is appropriate.

This is because the single-shaft wheel blades are produced in small quantities in many varieties, and therefore there is no economic advantage in forging or rolling. Therefore, it must be produced by casting and the casting method is an important manufacturing process.

There are various casting methods such as sand casting, die casting, precision casting and centrifugal casting, and there are advantages and disadvantages for each process. Abrasive wear resistance is the most important and Impact Strength is important for the wheel blades of the short wheel as the present invention. The mold casting method is the best method to satisfy both of them. The centrifugal casting method is better, but it is disadvantageous in terms of cost, such as equipment cost and mold cost.

For this reason, the present invention employs a mold casting method, and in particular, a special casting method is designed as shown in FIG. 3 for casting, gas defects, shrinkage voids, uniformity and fineness of the structure. The material of the mold is STD61 (SKD61), but only S15C or S20C.

The present invention dissolves the alloy at 1650 占 폚 in a high-frequency electric induction furnace because a high alloyed metal such as vanadium, tungsten, molybdenum, and niobium is alloyed with a large amount and a high temperature dissolution must be performed to obtain a uniform composition do.

The reason why the molten metal is injected into the mold at 1560 ° C is that the lower the injection temperature, the finer the crystal grains due to quenching, the more favorable in terms of strength and hardness, and excessively low in casting defects. Therefore, in our case, the injection temperature is around 1560 ℃.

The casting mold is air-cooled, demolded to obtain the product, and the product is normalized at 750 to 850 ° C for removing the casting stress.

The reason why the normalized product is heated and austenized (the explanation is unnecessary because it is the basis of heat treatment)

The reason for quenching an austenized product is oil quenching because of the risk of cracking in case of water quenching.

The reason for tempering oil quenched products is to release the thermal stress due to quenching and to temper hardness by tempering since it is high speed steel. In addition, tempering must be done to make the hardness distribution uniform.

In the mold of the present invention,

The reason for forming the large sprue is to make the sprue larger in order to speed up the injection rate and to increase the sprue because the sprue is replaced with the smaller one.

The injection port is formed by the upper injection port and the lower injection port in the case of the sugar blades, the upper and lower edges are thickened for assembling to the wheel. Therefore, the injection port should be installed in this area because there is a possibility of shrinkage hole defect in this part, and the two parts are divided into the upper part and the lower part so that the molten metal can be injected quietly without swirling.

The reason for the formation of the well is that when the molten material is directly injected into it, a vortex is generated. The bottom of the gutter serves as a buffer to reduce the flow rate and quietly flow the molten material into the inlet port, thereby preventing impurities such as slag from entering the product Because it acts as a giver.

The reason for installing the injection port on the wider side of the product in the blade mold space is that the injection port is connected to the sprue and the hot sprue enters the mold space through the sprue and becomes slow cooling. As a result, the organization becomes large. For sugar blades, the hardness of the end portion should be high, so the inlet must be installed on the wide side.

The reason for forming a vent hole at the end of the product is that when the mold fills the mold cavity through the injection port, the air in the mold cavity is compressed and the compressed air is backpressured to prevent entry of the mold. Therefore, a vent hole should be installed so that air can escape.

BEST MODE FOR CARRYING OUT THE INVENTION The present invention will now be described in detail with reference to the drawings.

FIG. 3 is a cross-sectional view illustrating a front casting method of the present invention, and FIG. 4 is a cross-sectional view illustrating a side casting method of the present invention.

In Fig. 3, the funnel shape at the center portion is a sprue (1). The product space 2 in which the plate-like shape of both sides is the blade of which the product is formed,

The wing shape connecting the central sprue 1 and the blade 2 is an injection port 3 and the injection port 3 is formed of an upper injection port 3-1 and a lower injection port 3-2.

The straw, which looks like a straw on both sides of the blade, is an unexpected hole (4), which discharges the gas generated by the injection of air and dirt from the mold space.

The sprue bottom 5 is formed in a concave shape to prevent the generation of vortices in the molten metal.

When the molten metal is injected through the sprue 1, the molten metal whose velocity is slowed down is filled into the product through the lower injection port 3-2 and the molten metal is injected into the product through the upper injection port 3-1, Thereby filling the mold space 2.

In this process, impurities such as slag and sand particles are left in the sprue, and only the clean sprue flows into the product space as the flow velocity is slowed, thus preventing the mixing of non-metal sprue and slag.

As seen from the side of FIG. 4, the inlet 3 has a cross-like shape without one side as shown in the drawing. The reason for this design is to prevent shrinkage defects. The injection port must be installed on the wide side of the product (the side where the short ball contacts first), and the upper injection port (3-1) and the lower injection port (3-2) are provided on the upper and lower ends.

Install the Vent Hole at the end of the product (the side where the short ball is projected). Rise is not installed. Injection needs to be injected quickly so that the tongue is enlarged and the tongue can also serve as the tongue. Because it is a vertically divided casting method, there is no separate runner. Instead, a well should be installed to prevent the occurrence of vortex.

Hereinafter, the present invention will be described in detail with reference to Examples.

Example

division                       Chemical composition State Landscape Heat treatment hardness  C Si Cr V Mo Co Nb W B execution mold execution mold
Example 1 2.1 0.8 3.2 3.8 18 25 1.0 2.5 3.0 HRC
63.1 HRC
66.5 HRC
66.2 HRC
68.5
Example 2 2.0 0.7 3.3 3.7 18 24 1.1 2.8 3.5 63.7 66.8 67.1 69.4
Example 3 2.4 0.8 3.5 3.2 17 25 1.0 3.0 3.0 63.5 66.8 66.5 69.0
Example 4 2.5 0.9 3.3 3.6 18 23 1.2 2.4 3.0 63.4 66.7 66.4 68.9
Example 5 3.0 0.7 4.0 4.0 17 23 1.0 2.6 3.0 65.0 67.5 67.7 69.5
Example 6 3.1 0.8 3.8 4.1 18 25 1.1 2.7 2.9 65.4 67.8 67.9 69.7
Comparative Example 1 3.0 1.0 4.0 10 8.0 3 6.0 2.0 - 60.9 62.1 64.7 65.8
Comparative Example 2 3.0 0.8 4.0 8.0 13 8 2.0 3.5 2.0 62.7 63.9 64.6 65.4 Comparative Example 3
(15Cr3Mo) 3.5 0.6 16 - 3.0 - - - - 60.0 62.1 63.5 65.1 Comparative Example 4
(HSS T15) 1.5 0.4 4.0 5 One 5 - 12 - - - *minor 65.9 Comparative Example 5
(Stellite 190) 3.2 1.0 27 - - 50 - 13.5 - 48.8 52.3 52.4 58.7 Comparative Example 6
(SKD11) 1.5 0.4 13 0.5 One - - - - - - *minor 64.3

Comparative Example No. 4 and Comparative Example No. 6 were not cast, but were forged or rolled.

Examples 1 to 6 are the inventions of the present invention

Comparative Example No. 1 is a high-vanadium and niobium-based alloy to which boron is not added, and a small amount of molybdenum and cobalt is also added.

Comparative Example No. 2 is a product obtained by slightly reducing boron, cobalt and molybdenum in the present invention.

Comparative Example No. 3 is a high chromium white cast iron, which is the most excellent in hardness and abrasion resistance among high chromium white cast iron.

Comparative Example No. 4 is an alloy having the highest abrasion resistance among ASTM standard high-speed steels (HSS), which is forged and rolled.

Comparative Example 5 is a material having the highest abrasion resistance among conventional stellite.

Comparative Example No. 6 is a material made by cold forging or rolling with cold metal steel SKD11 (KS STD11) which is JIS standard that is currently used for the longest time in the market.

In the heat treatments of Examples 1 to 6 of the present invention shown in Table 3, the casting stress was removed by performing normalizing heat treatment at 750 ° C at 850 ° C, and then the temperature was raised to 950 ° C to 1,050 ° C to subject the structure to austenizing Followed by oil quenching, and tempering heat treatment was performed at 530 ° C to 580 ° C for 2 hours.

Comparative Example No. 1 was osteonized at 950 ° C and subjected to oil quenching and tempering in the same manner.

Comparative Example 2 was subjected to quenching and tempering heat treatment in the same manner as in Example.

Comparative Example No. 3 was heated up to 1,050 ° C., subjected to air quenching after osteinization, and was not subjected to heat treatment.

Quenching and tempering were carried out according to the international standards in Comparative Examples 4 and 6.

In Table 3, Examples 1 to 6 show that the casting method is divided into sand casting and metal mold casting,

The die casting mold was made by CO2-process using sodium silicate as a binder, and the mold of the die casting was made of a carbon steel mold.

The dissolution was dissolved in a high frequency electric induction furnace. The maximum dissolution temperature was 1,650 ℃, and the injection temperature was 1,500 ℃ for die casting and 1,560 ℃ for mold. The reason why 60 ℃ higher temperature than injection mold casting is injected in mold casting is because the shape of product does not come out by quenching or wrinkles are formed on the product surface.

As a result of injection, the hardness of mold casting was higher than that of casting mold. This is because, as a result of the cooling rate, when the liquid metal solidifies in the mold, there is no time for the crystal grains to grow if the cooling rate is high, and the crystal grain size (grain size) becomes small. In addition, the Matrix is also becoming more martensite.

When the content of carbon in Examples 1 to 6 of Table 3 is increased, the hardness is also increased. Of course, increasing the boron content in the same chemical composition also increases the hardness. The hardness difference between mold casting and mold casting was about 2.5 point to 3.0 point.

Shock and wear test   division Hardness after heat treatment (HRC) Wear test (loss amount) Impact strength (Charpy)  Example 1 HRC68.5 (Mold Casting)   22.7 mg  7.2 ft-lbs  Example 2 HRC69.4 (Mold Casting)   19.7 mg  6.8 ft-lbs  Example 3 HRC69.0 (Mold Casting)   20.1 mg  7.0 ft-lbs  Example 4 HRC68.9 (Mold Casting)   21.6 mg  7.1 ft-lbs  Example 5 HRC69.5 (Mold Casting)   19.1 mg  6.2 ft-lbs  Example 6 HRC69.7 (Mold Casting)   18.8 mg  6.0 ft-lbs  Comparative Example 1 HRC65.8 (Mold Casting)   32.9 mg  7.2 ft-lbs  Comparative Example 2 HRC65.4 (Mold Casting)   29.8 mg  7.4 ft-lbs  Comparative Example 3 HRC65.1 (Mold Casting)   58.6 mg  6.8 ft-lbs  Comparative Example 4 HRC65.9 (Forging)   45.4 mg  12.1 ft-lbs  Comparative Example 5 HRC58.7 (Mold Casting)   66.1 mg  28.7 ft-lbs  Comparative Example 6 HRC64.3 (Forging)   74.3 mg  14.6 ft-lbs

As expected from the hardness test in Table 3 above, the abrasion resistance and impact strength

The results are shown in Table 4, which shows excellent abrasion resistance of the present invention having high hardness.

On the other hand, the impact strength is somewhat lower, which is inversely proportional to hardness and impact strength. Although the invention has a somewhat detrimental impact value compared to conventional products, there is no problem that it can be used as a shorting device.

1: sprue 2: blade 3: inlet
3-1: upper injection hole 3-2: lower injection hole 4: unfolding hole 5: sprue bottom

Claims (6)

Wherein the molybdenum (Mo) is 13 to 20%, the cobalt (Co) is 18 to 30%, the vanadium (V) is 3 to 6%, the chromium (Cr) is 3 to 5% 0.5 to 1.2% of silicon (Si), 0.1 to 0.5% of manganese (Mn), 2.5 to 4.5% of boron (B), 1 to 2% of niobium Nb and 1 to 2% of tungsten (Fe) and unavoidable impurities, and the balance is made of a material made of iron (Fe) and unavoidable impurities, and the balance of the rare earth metal (RE) is 0.1 to 0.2% , And the end portion has an impact strength higher than that of the inner portion. The wheel blade for a short-chain wheel having high hardness and high abrasion resistance The method according to claim 1,
Wherein the wheel blade has a bulk hardness value of HRC 67 to 68. The wheel blade for a short- Wherein the molybdenum (Mo) is 13 to 20%, the cobalt (Co) is 18 to 30%, the vanadium (V) is 3 to 6%, the chromium (Cr) is 3 to 5% 0.5 to 1.2% of silicon (Si), 0.1 to 0.5% of manganese (Mn), 2.5 to 4.5% of boron (B), 1 to 2% of niobium Nb and 1 to 2% of tungsten (Fe) in an amount of 0.1 to 0.3%, aluminum (Al) in an amount of 0.1 to 0.2%, titanium (Ti) in an amount of 0.1 to 0.3%, a rare earth metal (RE) in an amount of 0.1 to 0.2% Lt; RTI ID = 0.0 > 30 C, < / RTI >
Injecting the melted molten metal into a mold for casting a wheel blade at 1560 占 폚 占 10 占 폚,
Cooling the metal mold into which the molten metal is injected,
Normalizing the wheel blade at 750 to 850 ° C,
Elevating the normalized wheel blade to 1050 DEG C +/- 20 DEG C, subjecting it to austenizing,
Oil quenching the austenized wheel blades,
And a step of tempering the oil-quenched wheel blades. The method for manufacturing a wheel blade for a short shaft having high hardness and high abrasion resistance The method of claim 3,
Wherein the step of tempering comprises maintaining the wheel blade at 530 to 580 DEG C for 120 to 140 minutes. 1. A mold for manufacturing a blade of a vertically divided casting type comprising a casting mold for casting molten metal, an injection port for leading the casting mold to the casting mold, and a mold space of the blade product,
The sprue is largely formed so as to serve as a role of quick injection and air bubbling,
The injection port includes an upper injection port and a lower injection port,
A bottom surface for suppressing the generation of vapors in the molten metal is formed in the lower portion of the sprue,
Characterized in that the mold space of the blade product is formed such that a portion of the mold space where the shot ball first comes into contact with the injection port and a tip hole is formed at the end of the mold space to allow gas to escape. 6. The method of claim 5,
Characterized in that the upper injection port and the lower injection port have a shape in which the side surface of the upper injection port and the lower injection port have a cross shape and one surface is not provided.

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