UA66448A - A high-speed carburizing steel (variants) and a method for processing the cutting tool of the high-speed carburizing steel (variants) - Google Patents

Abstract

A high-speed carburizing steel contains carbon, silicon, chrome, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, cerium, sulphur, iron, nitrogen, manganese, copper, nickel and phosphorus. In the second embodiment the steel contains carbon, silicon, chrome, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, cerium, sulphur, iron, manganese, copper, nickel and phosphorus. In third, fourth and fifth embodiments the steel is different from the second embodiment by a quantitative composition of ingredients. A method for processing the cutting tool of the high-speed carburizing steel involves cementation, tempering, drawback. In the first embodiment the cementation is performed at the temperature of 900-1220 DEGREE c, with a carburizing medium carbon potential providing obtaining a carbon content of 0.6-1.5 % by weight in the carburized layer of blank or finished tool, tempering is performed from the temperature of 1170-1280 DEGREE c, and drawback is performed no more than three times at the temperature of 520-640 DEGREE c. In the second embodiment of the method, the first tempering is performed from the temperature of 1050-1350 DEGREE c before cementation, and the cementation is performed at the temperature of 900-1220 DEGREE c with the carburizing medium carbon potential providing obtaining a content of 0.6-1.5 % by weight in the carburized layer of blank or finished tool a carbon, the second tempering is performed from the temperature of 1170-1280 DEGREE c, and drawback is performed no more than three times at the temperature of 520-640 DEGREE c. In the third embodiment the first tempering is performed from the temperature of 1050-1350 DEGREE c before the cementation with a subsequent drawback at the temperature of 560-780 DEGREE c, and the cementation is performed at the temperature of 900-1220 DEGREE c, with the carburizing medium carbon potential providing obtaining a carbon content of 0.6-1.5 % be weight in the carburized layer of blank or finished tool, the second tempering is performed from the temperature of 1170-1280 DEGREE c, and drawback is performed no more than three times at the temperature of 520-640 DEGREE c.

Description

Description of the invention

The inventions are related to ferrous metallurgy, in particular to the production of high-speed steel and tools from it, can be used in the machine-building and tool industries when strengthening cutting tools from high-speed steels.

The claimed group of inventions refers to different objects, some of which are intended for the implementation of other objects, while the inventions included in the group are variants of the solution of the same problem in fundamentally the same way, which cannot be covered by one general claim. 70 The main object in the claimed group is cemented high-speed steel (options), the implementation of which is aimed at another object of this group - a method of processing a cutting tool from cemented high-speed steel (options).

The closest in technical essence and achievable result to the main objects of the group that are declared (cementable high-speed steel) is a matrix alloy containing carbon, silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron . 0.2 with 0.2-2.0 of 3.0-B0

M 1.0-20.0

In 1.0-8.0

Mo 2.0-10.0

So 1.0-15.0 ti 0.02-2.0 « 7g 0.02-2.0

Mo 0.05-2.0 in 0.001-0.005 z lanthanides 0.05-0.1 so 8 0.015-0.3 "

Her other "E

However, the specified alloy has a significant drawback - large carbides of irregular or (Ce) angular shape are found in the structure, which are the centers of carbide formation during subsequent cementation, which leads to an increase in carbide heterogeneity and distortion of the working edge of the tool during operation, which means to reducing the stability of the tool.

The proposed inventions are based on the problem of qualitatively increasing the stability of a tool made of high-speed steel by obtaining, in the process of subsequent cementation and heat treatment, the working and carburized layer of the tool with uniformly distributed dispersed or plate-rod special carbides. This task is solved by selecting the composition of high-speed steel, which is cemented. :z" In the first version, the problem is solved by the fact that the known matrix alloy, which contains carbon, silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanides, sulfur and iron, additionally contains nitrogen, manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with b" 395 the following ratio of components (weight, 95):

Ge") with no more than 0.3

Sg 3.0-5.0 e M 2.5-13.0 iz 50 U 1.0-8.0

Mo 2.0-10.0 with MP 0.1-0.8 with 0.1-2.0

Those are no more than 2.0

Sy not more than 0.3 in. Mi is not more than 0.6

With no more than 0.035

P not more than 0.035 60 M not more than 0.5 and not more than 0.1 in not more than 0.05

This is no more than 0.1

So no more than 3.0 65 M 0.04-0.6

It's different

In the second version, the problem is solved by the fact that the known matrix alloy, which contains carbon, silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanides, sulfur and iron, additionally contains manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with the following ratio of components (weight, 90): c no more than 0.3

SG 3.0-5.0

M 2.5-13.0

M 1.0-8.0

Mo 2.0-100

MP 0.1-0.8 with 0.1-2.0

Those are no more than 2.0

Sy is not more than 0.3

Mi is not more than 0.6

With no more than 0.035

P not more than 0.035

M is no more than 0.5 and no more than 0.1 in no more than 0.05

This is no more than 0.1

So no more than 3.0

Be different "

In the third version, the task is solved by the fact that the known matrix alloy, which contains carbon, silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanides, sulfur and iron, additionally contains manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with the following ratio of components (weight, 90): "c not more than 0.3

Sg 3.0-5.0 t

M 8.5-20.0 (so)

M | 1.0-8.0 s

Mo not more than 2.0

MP 0.1-0.8 with 0.1-2.0

Those no more than 2.0 "

Si no more than 0.3 shsh with Mi no more than 0.6

Z no more than 0.035: z» P no more than 0.035

M is no more than 0.5 and no more than 0.1

Ge") in no more than 0.05

Se no more than 0.1 and Co no more than 3.0 s» Re other iz 50 In the fourth variant the task set is solved by the fact that a matrix alloy containing carbon, silicon, chromium, tungsten is known , vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanides, sulfur and iron, additionally contains manganese, copper, nickel and phosphorus, and cerium as lanthanides, with the following ratio of components (weight, 90): more than 0.3

R Сg 3.0-5.0

M MO 2.5-13.0 1.0-8.0

Mo 2.0-100 in Mp 0.1-0.8 with 0.1-2.0

Those are no more than 2.0

Sy is not more than 0.3

Mi not more than 0.6 65 C not more than 0.035

P not more than 0.035

M is no more than 0.5 and no more than 0.1 in no more than 0.05

This is no more than 0.1

So 3.0-12.0

It's different

In the fifth variant, the problem is solved by the fact that the known matrix alloy, which contains carbon, 70 silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanides, sulfur and iron, additionally contains manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with the following ratio of components (weight, 90): c no more than 0.3

SG 3.0-5.0

M 8.5-20.0

In 1.0-8.0

Mo not more than 2.0

MP 0.1-0.8 in 0.1-2.0

Those are no more than 2.0

Sy is not more than 0.3

Mi is not more than 0.6

With no more than 0.035

P not more than 0.035

M is no more than 0.5 " and no more than 0.1 in no more than 0.05

Se is not more than 0.1 (ee)

So 3.0-12.0

Her other With "

The method of processing a cutting tool made of high-speed steel, which includes ise) is the closest in terms of technical essence and achievable result to the method of processing the cutting tool that is claimed

From two-stage homogenizing treatment in a decarburizing environment, high-temperature cementation, hardening and tempering (A.E. USSR Mo850703, C2109/22, C2101/78, Byul. Mo28, 1981). According to this method, the tool is subjected to a two-stage homogenizing treatment at 1270-1280" and 1310-1320"C in a decarburizing environment, then high-temperature cementation and final heat treatment - quenching and tempering are carried out. Decarburization at 1270-1280" ensures the production of a low-carbon shell, which is necessary to "prevent the growth of molten eutectic, which is formed at 1310-1320"С, which makes it possible to obtain a ferrite layer of two to three millimeters in a relatively short time in which eutectics are completely absent carbides The subsequent carburization of the decarburized surface makes it possible to obtain in the surface layer a structure with ;" finely dispersed, evenly distributed carbides, which provide high cutting properties and wear resistance of the cutting tool after final heat treatment.

However, the presence of carbide eutectic in the core of the tool reduces its strength, especially in the tool

F of a significant cross section.

The proposed inventions are based on the problem of qualitatively increasing the stability of a tool made of high-speed steel, due to the presence of a viscous low-carbon core in the tool and the use of a wear-resistant, carburized working layer obtained in the process of cementation and final heat treatment with uniformly distributed dispersed or plate-rod special carbides , excluding complex high-temperature homogenizing treatment. This task is solved by selecting pretreatment modes, cementation modes, and final heat treatment modes.

In the first version of the method of processing a cutting tool, the task is solved by the fact that there is a known method of processing a cutting tool from high-speed steel, which includes carburizing, hardening, tempering, etc. It is carried out as follows: carburizing is carried out at a temperature of 900-1220"C, with the carbon potential of the carburizing medium , which ensures obtaining a blank or finished product in a carbonized layer

The carbon content of the tool is 0.6-1.5 wt. 956, tempering is carried out at a temperature of 1170-1280"С, and tempering is carried out no more than three times at a temperature of 520-64076.

In the second version of the method of processing the cutting tool, the task is solved by the fact that the method of processing the cutting tool from high-speed steel, which includes case hardening, hardening, tempering, includes an additional operation - before case hardening, the first case is quenched from a temperature of 1050-1350 C, case case carried out at a temperature of 900-12207C, with the carbon potential of the carburizing medium, which ensures obtaining a carbon content of 0.6-1.5 wt in the carburized layer of the workpiece or finished tool. 956, the second tempering is carried out at a temperature of 1170-12807C, and tempering is carried out no more than three times at a temperature of 520-640"C.

In the third version of the method of processing the cutting tool, the task is solved by the fact that the known method of processing the cutting tool from high-speed steel, which includes cementation, hardening, tempering, contains an additional operation - before cementing, the first tempering is carried out from a temperature of 1050-1350" followed by tempering at a temperature of 560-780, cementation is carried out at a temperature of 900-1220"C, with the carbon potential of the carburizing medium, which ensures obtaining a carbon content of 0.6-1.5 wt in the carburized layer of the workpiece or finished tool. 96, the second tempering is carried out at a temperature of 1170-1280"C, and tempering is carried out no more than three times at a temperature of 520-64076.

The common features of all the options of cemented high-speed steel, which are declared, and the prototype, are the presence of carbon, silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, 70 zirconium, niobium, boron, lanthanides, sulfur and iron in the composition of the steel.

Distinctive features of the first proposed variant and the prototype are that the steel additionally contains nitrogen, manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with the following ratio of components (weight, Ob): c no more than 0.3

SG 3.0-5.0

M 2.5-13.0

In 1.0-8.0

Mo 2.0-10.0

MP 0.1-0.8 in 0.1-2.0

Those are no more than 2.0

Sy is not more than 0.3

Mi is not more than 0.6

With no more than 0.035

P not more than 0.035 "

M is no more than 0.5 and no more than 0.1

In no more than 0.05 (ee)

This is no more than 01

So no more than 3.0 Z

M 0.04-0.6 "

Her other so

Distinctive features of the second variant claimed and the prototype are that the steel additionally contains (se) manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with the following ratio of components (weight, Ob): c no more than 0, 3"

Sg 3.0-5.0 ssh s M 2.5-13.0 y U 1.0-8.0 "» Mo 200-100

MP 0.1-0.8 in 0.1-2.0 (there are) They are no more than 2.0, but no more than 0.3

Mi not more than 0.6 t. 8 not more than 0.035 iz 50 R not more than 0.035

M not more than 0.5 s and not more than 0.1 v not more than 0.05

Se no more than 0.1 52 So no more than 3.0 in Ee other

Distinctive features of the third variant that is claimed and the prototype are that the steel additionally contains manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with the following ratio of components: 60 "weight, bo): c no more than 0.3

SG 3.0-5.0

M 8.5-20.0 65 U 1.0-8.0

Mo not more than 2.0

MP 0.1-0.8 in 0.1-2.0

Those are no more than 2.0

Sy is not more than 0.3

Mi is not more than 0.6

With no more than 0.035

P not more than 0.035

M is no more than 0.5 and no more than 0.1 in no more than 0.05

This is no more than 0.1

So no more than 3.0

It's different

Distinctive features of the claimed fourth variant and the prototype are that the steel additionally contains manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with the following ratio of components (weight, Ob): c no more than 0.3

SG 3.0-5.0

M 2 5-130

In 1.0-8.0

Mo 2.0-10.0

MP 0.1-08 in 0.1-2.0 "

Those are no more than 2.0

Sy is not more than 0.3

Mi not more than 0.6 (ee) 5 not more than 0.035 r o not more than 0.035 Z

MO not more than 0.5 chI and not more than 0.1 in not more than 0.05 sho

Se no more than 01 (se)

So 3.0-12.0

It's different

Distinctive features of the fifth variant that is claimed and the prototype are that the steel additionally contains "manganese, copper, nickel and phosphorus, and as lanthanides - cerium, with the following ratio of components - c (weight, Ob): c c not more than 0.3

SG 3.0-5.0

M 8.5-20.0

Gee! In 1.0-8.0

Mo not more than 2.0

Ф Mp 0.1-0.8 s» with 0.1-2.0 and 50 Those not more than 2.0

Si not more than 0.3 (Che) Mi not more than 0.6

With no more than 0.035

P not more than 0.035

МБ not more than 0.5 » and not more than 0.1 in not more than 0.05

This is no more than 0.1

So 3.0-12.0 because Ee is different

Common features of all the options for processing a cutting tool made of cemented high-speed steel, which are claimed, and the prototype, are cementation, hardening and tempering of the high-speed steel.

Distinctive features of the first variant of the method of processing a cutting tool made of high-speed steel, which is 65 cemented, which is claimed, is that the cementation is carried out at a temperature of 900-1220 °C, with the carbon potential of the carburizing medium, which provides the carbon content in the carburized layer of the workpiece or the finished tool 0.6-1.5 wt. 95, tempering is carried out at a temperature of 1170-1280 C, and tempering is carried out no more than three times at a temperature of 520-64076.

Distinctive features of the second variant of the method of processing a cutting tool made of high-speed steel, which

Carburized, which is claimed, is that before carburizing, the first quenching is carried out at a temperature of 1050-135092C7, carburizing is carried out at a temperature of 900-1220C, with the carbon potential of the carburizing medium, which ensures that the carbon content of the workpiece or finished tool is obtained in the carburized layer of 0, 6-1.5 wt. 956, the second tempering is carried out at a temperature of 1170-12807C, and tempering is carried out no more than three times at a temperature of 520-64076.

Distinctive features of the third variant of the method of processing a cutting tool made of cemented high-speed steel, which is claimed, are that before cementing, the first quenching is carried out at a temperature of 1050-135092С7 with subsequent tempering at a temperature of 560-7807"С, cementation is carried out at a temperature of 900-1220 "C, with the carbon potential of the carburizing medium, which ensures obtaining a carbon content of 0.6-1.5 wt in the carburized layer of the workpiece or finished tool. 96, second tempering 75 It is carried out from a temperature of 1170-1280"C, and tempering is carried out no more than three times at a temperature of 520-64076.

According to the information available to the authors, the set of features that are claimed, which characterize the essence of the variants of cemented high-speed steel and the variants of the method of processing a cutting tool made of cemented high-speed steel, are unknown at the state of the art. Therefore, the claimed inventions meet the "novelty" criterion.

The limits of content of chemical elements in the composition of high-speed steel, which is cemented in all variants, is justified by the following:

Iron. Cemented high-speed steel is an iron-based alloy.

Carbon. The amount of carbon in the cemented high-speed steel should not exceed 0.395.

The presence of carbon in the cemented high-speed steel has a negative effect on the ferrite-carbide state of the steel after reaching the cementation heating temperature (Fig. 1). An increase in the amount of carbon above 0.395 leads to partial austenitization of the steel and the presence of large carbides in the steel structure, which are the centers of carbide formation during subsequent cementation, which increases the carbide heterogeneity of the steel, which is not eliminated by further heat treatment, the consequence is a decrease in the stability of the finished tool, due to chipping working edge. (se)

Chrome. Chromium in high-speed steel is used to increase hardenability and, to a lesser extent, heat resistance. Its number is in the range of 3.0-5.096, which ensures the hardening of the tool of sufficiently large sizes. During tempering, chromium is partially released from martensite in the form of carbides, increasing dispersion hardening, and partially remains in the "Z" phase, delaying the weakening of steel at higher heating, thereby increasing heat resistance. Exceeding the upper limit of the amount of chromium does not lead to an improvement mechanical and technological properties, and, on the contrary, participating in the formation of (Ce) carbide, released during tempering, chromium facilitates its coagulation at a lower temperature, which reduces heat resistance. A lower amount of chromium (less than 3.090) does not provide conditions for a more complete dissolution of carbide MeS, when heating the steel for hardening, and accordingly leads to a decrease in the level of secondary hardness.

Vanadium. Vanadium in the composition of cemented high-speed steel provides an increase in the secondary hardness and heat resistance of the cemented tool. The optimal amount of vanadium should be 1.0-8.0905. and Vanadium ensures the formation of MS carbide in the structure of the carbonized layer. Low-soluble in austenite "» MC carbide contributes to the preservation of fine grain during heating of the cemented tool during quenching and increases its wear resistance and reddening resistance. When the amount of vanadium in the carburized layer of high-speed steel is up to 1.095, it is present in MozSv and MC carbides, which does not improve the technological and operational (e)) properties of the tool. When increasing the amount of vanadium above 8.095 in the structure of the carburized layer (when the amount of carbon in the layer is up to 1.595), the amount of MC carbide saturating the solid solution decreases when heated to quenching. As a result, in the structure of the carburized layer possibly the presence of ferrite, which

Cheka" has a negative effect on the stability of the instrument. In addition, a large amount of MC carbide greatly impairs the grindability of steel.

Manganese. Manganese in the high-speed steel, which is cemented, prevents the formation of low-melting steel

IR e) of sulfide eutectic, which leads to red brittleness of steel, binding sulfur into refractory manganese sulfide, and also increases the hardenability of a carburized tool, which is especially important when hardening a tool using advanced heat treatment methods, for example, gas quenching. 5B The amount of manganese in the cementitious high-speed steel should be 0.1-0.895. A reduced amount of manganese (below 0.195) has little effect on the properties of cemented high-speed steel. Exceeding this limit (more than 0.895) leads to an increase in the amount of residual austenite in the structure of the cemented and heat-treated tool, which reduces the hardness of the finished tool, and therefore worsens its stability. 60 Silicon. As the amount of silicon in the cemented high-speed steel increases, it increases the hardenability of the carburized tool. The amount of silicon in steel should not exceed 2.095. An increase in the amount of silicon above 2.095 impairs the machinability of the steel by cutting and contributes to the decarburization of the tool during subsequent heat treatment. A reduced amount of silicon (below 0.195) does not significantly affect the properties of the steel. 6E Titan. The amount of titanium in the cemented high-speed steel should not exceed 2.095. As the amount of titanium in the steel composition increases to 2.095, it forms carbides in the carburized layer that are very stable when heated, which reduce the tendency of the steel to grow grains, which allows you to increase the heating temperature for quenching, thereby increasing the degree of alloying of austenite, which leads to an increase in the level of the secondary hardness of the finished tool, which means its stability. However, when the amount of titanium is higher than 2.090, the formation of carbides occurs along the grain boundaries, which reduces the operational properties of the finished tool.

Copper. The amount of copper in cemented high-speed steel should not exceed 0.395. As the amount of copper in the steel composition increases to 0.395, it, reducing the mobility of carbon, contributes to the formation of small dispersed carbides in the steel structure during crystallization, which positively affects the formation of 76 carbides during carburization. In larger quantities, more than 0.395, copper slows down the rate of carbon diffusion, which leads to a significant slowing down of the cementation process.

Nickel. The optimal amount of nickel in the cementitious high-speed steel should not exceed 0.695. As the amount of nickel in the steel increases, up to 0.695, it helps to increase the hardenability of the cemented tool. Exceeding this limit leads to an increase in the amount of residual austenite in the structure of /5 Cemented and heat-treated tool, which worsens its stability.

Sulfur. The amount of sulfur in cemented high-speed steel should not exceed 0.03595. Otherwise, a low-melting sulfide eutectic is formed in the structure of the steel, which leads to red brittleness of the steel, thereby worsening its technological properties.

Phosphorus. Phosphorus, being an impurity in the composition of most steel brands, enters the composition of steel from the starting charge materials during smelting. The amount of phosphorus in the cemented high-speed steel should not exceed 0.03595. Otherwise, phosphorus reduces the work of crack propagation, which leads to a decrease in the viscosity of the finished tool.

Niobium. Zirconium. Boron. Cerium. Niobium in the amount of up to 0.595, zirconium in the amount of up to 0.195, boron in the amount of up to 0.0595, and cerium in the amount of up to 0.195 eliminate the heterogeneity of cemented steel when heated under quenching. Exceeding the above-mentioned quantity limits is not only economically impractical, but also leads to a decrease in the technological plasticity of high-speed steel. "

Tungsten. Molybdenum Tungsten and molybdenum, being chemical analogs, exert almost the same effect on the properties of high-speed steels.

Molybdenum, due to its effect on the heat resistance of high-speed steel, replaces tungsten in the ratio of Mo:Mu-1:1.5 (Heller Yu.A. Instrumental steels. M.: Mashinostroenie, 1983. p. 363) Tungsten, together with molybdenum, in composition of cemented high-speed steel, provides the necessary secondary hardness and heat resistance of the steel, due to the formation of special carbides during subsequent cementation in the working layer of the tool (mainly "g

Me).

The amount of tungsten in tungsten high-speed steel containing up to 295 molybdenum should be ise) 8.5-20.095 (third and fifth options). This amount of tungsten ensures the presence of MeS carbide in the structure of the carburized layer of the tool. When the amount of tungsten in tungsten steel is below 8.595, after cementation, the carbide phases are represented by a large amount of carbide M 2zSv, soluble when heated during quenching, which negatively affects the resistance of the steel against overheating, and as a result, the viscosity of the steel decreases sharply. Increasing the amount of tungsten in tungsten high-speed steel above 2095 requires "

Increasing the tempering temperature of the cemented tool, for more complete dissolution of carbide M vs. However, such an increase in the tempering temperature is impossible due to eutectic melting. Therefore, the increase. amount of tungsten more than 2095 does not lead to an increase in the concentration of tungsten in the solid solution at heating during quenching, and therefore dispersion hardening of steel does not proceed more intensively during the next tempering. At the same time, increasing the amount of molybdenum to 295 continuously increases the viscosity and strength of the heat-treated tool, without changing its heat resistance.

Ge» The amount of tungsten in tungsten-molybdenum high-speed cutting steel containing up to 1095 molybdenum (first, second and fourth options) should be 2.5-13,090.

Me. A decrease in the amount of tungsten below the lower limit (2.595) leads to a decrease in the melting temperature of the eutectic, which leads to a decrease in the temperature of heating the cemented tool during hardening, and, therefore,

A decrease in the level of secondary hardness, which ultimately leads to a decrease in tool stability. The upper limit of the amount of tungsten in tungsten-molybdenum high-speed cutting steel is justified by the fact that the stability of a tool containing more than 13.095 tungsten is at a sufficient level without additional doping with molybdenum (more than 2.090).

When tungsten is partially replaced by molybdenum in the composition of tungsten-molybdenum high-speed steel, its optimal amount is determined using the empirically obtained formula: УУк1.4-1.5Мо-12-1490.

High-speed steel with a molybdenum content of more than 1095 has increased sensitivity to decarburization and

P of grain growth when heated during tempering, which leads to a decrease in the stability of the tool.

Cobalt. Cobalt increases the heat resistance and secondary hardness of cemented and heat-treated tools by increasing the stability of the solid solution against weakening during heating, and it also contributes to a more complete release of tungsten and (or) molybdenum from martensite during tempering, due to a decrease in the solubility of these elements in the o-phase. thereby increasing the secondary hardness and improving thermal conductivity, which increases the stability of the tool. Cemented high-speed steel (options one, two, three), after heat treatment, is a steel of moderate heat resistance. The amount of cobalt in these steels should not exceed 3.095. At the same time, increasing the amount of cobalt to 395 continuously increases the thermal conductivity of the heat-treated b5 tool, which reduces the heating of the working edge of the tool, increasing its stability. An increase in the amount of cobalt in the indicated variants of cemented high-speed steel above 396 is unjustified, because it transfers the steel to the category of steels of increased heat resistance, used when cutting materials in the absence of increased dynamic loads.

The amount of cobalt in cemented high-speed steel (options four and five) should be in the range of 3.0-12.096. When increasing the amount of cobalt in steel above 1295, MC carbide will form in the structure of the carburized layer, which reduces heat resistance, and therefore the stability of the tool as a whole. In addition, a high amount of cobalt (above 1295) leads to reduced hot plasticity of steel.

Nitrogen. Nitrogen, in the amount of 0.04-0.696, which is additionally found in the composition of high-speed steel that is cemented, according to the first option, contributes to the formation of finer austenite grains when heated during hardening of the carburized tool, which allows to increase the temperature of heating the tool during hardening, to warn grain size of steel, increase the secondary hardness and heat resistance of the tool.

The amount of nitrogen less than 0.0495 is ineffective, as no excess hardening phases (nitrides and carbonitrides) are formed. The amount of nitrogen above 0.4595 reduces the hardness of the tool after heat treatment due to the appearance of a carbonized layer of the carbonitride mesh in the structure.

Cementation according to all variants of the method of processing a cutting tool made of high-speed steel, which is cemented, is carried out at a temperature of 900-1220 "C, with a carbon potential of the carburizing medium, which ensures obtaining a carbon content of 0.6-1.5 wt in the carburized layer of the workpiece or the finished tool. 965. This is justified by the following:

Cementation of the tool at a temperature below 9007C leads to the formation of an undesirable carbide mesh, located at the boundaries of ferrite grains, which is not soluble when heated for hardening, which leads to a decrease in the stability of the finished tool. Cementation at a temperature above 1220"C leads to the danger of melting of the tool blanks, especially tools of a complex shape with sharp edges. A decrease in the amount of carbon in the carburized layer (below 0.690) leads to a decrease in the amount of carbide phase in the layer, which leads to a decrease in the stability of the tool. Increasing the amount carbon over 1.595, due to the increase in the amount of the carbide phase, leads to a decrease in the viscosity of the finished tool. In addition, such an excess of carbon can lead to melting of the tool blanks when heated to the tempering temperature.

Tempering according to all variants of the method of processing a cutting tool made of cemented high-speed steel is carried out after cementation and hardening, carried out no more than three times at a temperature of 920-640 "C. At the same time, a part of carbon and alloying elements in the form of carbides are released from austenite. depleted austenite undergoes a transformation into martensite during cooling, which leads to an increase in the hardness and strength of the tool. Repetition of tempering from one to three times contributes to a more complete transformation of residual austenite into martensite. The positive role of multiple tempering is that it increases resistance plastic deformation. In addition, the viscosity and strength of the tool increase. An increase in the number of temperings more than three times is unjustified, because it does not lead to an increase in the stability of the tool due to the small (less than 25905) amount of residual austenite in the carburized layer already after the previous multiple leave.

Tempering at a temperature below 5207C does not lead to the release of carbides, the residual austenite is very stable and does not undergo transformation during subsequent cooling, which reduces the hardness of the finished tool. More "high tempering (above 640"C) causes martensite disintegration, leads to the release of carbides in the boundary pt") with grain interlayers, which reduces the hardness and durability of the finished tool.

Additional preliminary processing, which is carried out according to the second variant of the cutting tool processing method;" from cemented high-speed steel, which consists in hardening (before cementing) from a temperature of 1050-13507C, contributes to the formation of a uniform structure of steel before cementing, which provides an increase

Contact durability of the surface cemented layer due to the dissolution of excess carbides and

Homogenous distribution of alloying elements in steel before carburizing. Such processing allows forming a carbide phase of plate-rod morphology during the cementation process, which provides increased stability

Me, a tool. Lowering the tempering temperature below 10507C leads to incomplete dissolution of their carbide phase, which negatively affects the stability of the tool. Tempering from a temperature above 13502 leads to significant grain growth, which worsens the technological plasticity of steel. shk Additional preliminary treatment, carried out according to the third variant of the method of processing a cutting tool made of cemented high-speed steel, which consists in hardening (before cementation) from a temperature of 1050-1350" with subsequent tempering at a temperature of 560-7807C, contributes to the formation of a uniform steel structure before cementation, which ensures an increase in the contact durability of the surface cemented layer, due to the release during tempering of a finely dispersed, uniformly distributed phase. The finely dispersed structure previously prepared in this way determines the cementation process with the formation of a strengthened » layer, characterized by the absence of any carbide heterogeneity. A decrease in the tempering temperature below 560"C leads to incomplete separation of the carbide phase from ferrite, and an increase in the tempering temperature above 7802 leads to coagulation and coarsening of the carbide phase, which reduces the stability of the finished tool. 60 The essence of the claimed inventions does not follow by any stretch of imagination from the state of the art known to the authors. The set of features that characterize known solutions do not ensure the achievement of new properties, and only the presence of the listed distinguishing features allows obtaining a new technical result.

Therefore, the claimed inventions (options) meet the "inventive level" criterion.

The claimed inventions are explained by graphic images: 65 Fig.1. The influence of the initial amount of carbon in the composition of cemented high-speed steel on the secondary hardness of the carburized and heat-treated tool, with the following chemical composition of the steel: St-4.2965;

MU-8,390; Mo-5,090; M-5,690;

May-0.690; 5i-1,590; Ti-1,595; Sy-0.2590; Mi-0.495; 5-0.0290; P-0.0290; МБ-0.3590; 21-0.0590; B-0.0390; Ce-0.0890;

Co-2,1 90; Re - other;

Fig. 2. The effect of the amount of titanium in the cemented high-speed steel on the secondary hardness of the carburized and heat-treated tool, with the following chemical composition of the steel: C-0.1590; St-4.7905;

MU-8,390; Mo-5,095; M-5,690; MP-0.6b90; 5i-1,590; Sy-0.2590; Mi-0.490; 5-0.02590; P-0.0290; МБ-0.3590; 21-0.01905;

B-0.0390; Ce-0.0895; Co-0.1590; Re - other;

Fig. 3. The effect of the amount of copper in the cemented high-speed steel on the size of the carbide particles and the depth of the carburized layer (sh), with the following chemical composition of the steel: C-0.290; St-4,790; MU-6,390;

Mo-5,090; M-3,690; Mi-0, b9o; Z-0.590; Ti-1,590; Mi-0.21905; Z-0.02590; P-0.01595; MB-0.0590; 21-0.0190; B-0.01905;

Ce-0.0195; Co-0.1090; Re - other; at cementation temperature Tc-1050 "C; within "-1 hour;

Fig. 4. The influence of the amount of nickel in the composition of high-speed steel that is cemented on the hardenability (x) and the amount of residual austenite in the carburized layer of cemented steel after quenching from 1220 "C (g), 75 with the following chemical composition of the steel: C-0.2290; St- 3.590; MU-5.390; Mo-5.590; M-2.690; Mpy-0.790; 8i-1.590; Ti-0O.590;

Sy-0.2590; 5-0.025905; P-0.025905; МБ-0.00590; 21-0.00595; B-0.0195; Ce-0.0190; Co-1,690; Re-other;

Fig. 5. The effect of the amount of alloying element in the composition of high-speed steel that is cemented on the grain size of the carburized layer after quenching from 1230 "C of the cemented tool: x is the effect of boron (C-0.1390; St-3.190; M/-5.895; Mo-5.590; M-2.695; Mn-0.4965; z-0.3590; Ti-0O.690; Cy-0.2590; Mi-0.5190; 5-0.0390; P-0.03905; Mb-O, 0190; 2-0.190; Ce-0.01905; Co-0.6090; Re - other) w - influence of zirconium (C-0.14905; St-3.590; MU-5.690; Mo-5.790; M-1.990;

May-0.490; Z5i-0.3590; TiI-0O,690; Sy-0.2190; Mi-0.5190; 5-0.03905; P-0.0390;

МБ-0.01905; 8-0.0195; Se-0.01905; Co-0.9090; Re - other) "- influence of niobium (C-0.1090; St-4.590; MU-5.690; Mo-5.890; M-1.695; Mp-0.490; " with-0.3590; Ti-0.995; Sy-0, 2590; Mi-0.45905; 5-0.0390; P-0.0390; 21-0.0990;

B-0.0195; Se-0.195; Co-0.90905; Re - other)

A - influence of cerium (C-0.09905; St-4.990; M/-6.195; Mo-5.8905; M-1.890; Mp-0.4590; Z-0.2590; Ti-1.695; Sy-0, 1590; Mi-0O,35905; 5-0.0390; P-0.0390; 21-0.0990; so

B-0.0196; 71-0.0996; Co-1.5 95; Ge - other) "U

Fig. 6. The influence of the amount of molybdenum in the composition of cemented tungsten high-speed tungsten steel on the impact toughness of the carburized and heat-treated tool, with the following chemical composition of the steel: C-0.24905; St-3,290; MU-16,8905; M-2,690; Mpy-0, b90; 5i-1,595; Sy-0.2590; Ti-1.8905; Mi-0.490; 5-0.02590; (Se)

P-0.02905; МБ-0.3590; 21-0.0195; B-0.0390; Ce-0.0895; Co-0.1590; Something else.

Examples of concrete implementation of

The chemical composition of the cemented high-speed steel (variants), which is claimed, and the known matrix alloy (prototype) are given in the table. 1, and the results of technical tests in table. 2.

The claimed high-speed, cementitious steel was melted in a laboratory induction furnace "

LI3-67 is based on Armco-iron with the addition of appropriate industrial ferroalloys and poured into ingots 7 70 two mm, 1-350 mm. with ;" (22) (22) street 50

IR e)

R

60 b5

Table

The chemical composition of cemented high-speed steel (options), which is claimed, and the matrix alloy (prototype). the state is about 1 - 128122 | 103 08 10051008! - | - 7 - 1-2 10005) 30 | 25 | 100 10 | 01 | 01 1000110001| 001 1-3 1001) 3.8 15251 65 | 29 10351 08 | 05 | 015 01 (14 015 42 83 | 50 | 56 1 06 | 15 | 15 | 025 | ohm from 11503150 11301 20 | 80 ) 08 | 20 | 20 | oz | 06 161|035| 56 | 138 16 | 83 | 086) 24 231 | 035 | 02 2411 - | 28 | 22 | 103 08 10051008 - | - | - th 12-2 105005| 30 | 25 | 100 10 HER 01 | 0 00011 0.001| 01 23 1001| 3.8 | 5225 6.5) 29 1035) 08 1 05 015| 0 (24 015 42 | 83 | 50 | 56 | 06 | 15 | 15 1025 04 2-5 03 | 50 | 130| 20 | 80 | 08 | 20 20 03 06 341 - 1281801 - | 08 |0051008| - her - Ii - 3210005) 30 | 855 0011 10 | 01 in bl |000110001) 001 331001) 38 130 05 | 29 | 0351 08 | 05 | 05 | 0 | so from 3-4 | 0415 42 | 180 | 15 | 56 06 15 | 15 10251 04 35103150 200 20) 80 | 08 20 120 | 03 | 06. h h

F

41 - | 2822 103108 | 0050081 - 1. | - 7 Gaz» 1о0005| 30 | 25 100! 10 o'clock 0 (0001100011 001 | o (43 | 001 3.8 5.225 65 | 29 1035 08. 0.5 015 0 (45103) 50 1130 20 80) 08 1 20 20 | 03) 06 | h sera and me n- s 5 option

And" kl shi shshitnnnin niSny siva myshiI

And 5-2 10005130) 85 | 001| 10 | 01 | 01 1 000110,001| 001 tya 1531001 38 | 130 | 05 | 29 | 0351 08 | 05 | 015| 0

F 5-4 5 la vo te I 11 1 5 BV

Ann Liny Nih Nki 290 103106.

Ф 5-6 5.6 ve Well-known matrix alloy (prototype) auto. Lo513113 o | pi0151 30 1591 67123 | - | 123 | 096 n- :

P-2 | 017 6.3 - AND 1121 -

IR e)

R" 60 65

Continuation of table 1.

Content of elements, 95 kg. composition 715141 in | M | and | in | That's it So | m | ke 41 - 1-1 - 1-1 - 1-1 - 1003 others. 1-2 |00051 00050001 0001) 00010001 | 0001) 004 other. "173 Gobi o001 1051001 | 001 | 001 | 05 02 | other Other | 035 | 005 | 003 | 008. 20 - | others 71725 00350351 05 | 01 10051 01 1 30 | - | others 26 00400040) 0.55 | 01z | 0053 0115 / 31 | - | others 31 1-1 - 1-1 - 1-1 - 1-1 - others 251 352 00050005 1 0001|0001| 00011 0001 0001| - And! others | « 33 | 001 | 001 | 05 | 001 |) 001 | 001) 015 | - | others 34 | 0021 002 | 035 | 005 | 003 | 008 | 20 | - others 3-5 0035) 00351 05 | 01 | 005 | 01 | 30 | - others from 1-36. 100401 0040) 055 | 0iz | 0053| 015 | ЗМ | - other |. so -

A r - 17-17 - 1-1 - 1-23 | - others « az 10005 0005| 0001/0001 00011 0001) 30 | - / others az | 0011 0011 015 | 001 001 | 001 1 49 | - | others | schi zb | 44 002 1 002 | 035 | 005 | 003) 008 | 73 | - | others | se) 0035100351 05 | 01 1 005 01 1120 | - | others 46 |0040|0040) 055 | 013 | 0053 015 | 126 1 - | others « i 5 HER - 1-1 1-11 125 - | etc. With se 17752 | 0005 000510001|0001| 00010001 30 | - | others and 53 | 00110011 0151001 | 001) 0011 49 - | others 6154 1002 | 002 03510051 003 | 008) 73 | - in others 5-5 Sh|0035 0035, 05 01 | 0051 01 | 120 | - | ate -5 | 56 100401 0040) 055 | 013 | 0053 015 | 126 | - | others

F

F li 10032) - | 005 | 003 004 005 | Ize | - in |. p? 10031 - | 005 | 003 | 0os4| 005 | 53 | - | others driving (prototype).

Me composition Me composition i TT ENN NN NN I » in 65 2-2 5О?2 20.1 5-2 690 23.5 in vv01yaya1 nn shk i hi po PO PO o ve117111juv 17711311

Ingots were forged on a 918 -20 mm bar. M12 machine-hand tap blanks were obtained from forged bars by a mechanical method or by the method of radial 75 stamping.

Cementation of tap blanks was carried out in a laboratory vacuum cementation furnace in an environment of methane or acetylene at a temperature of 10507C, for 3 hours, at a pressure of 15-20Pa. The average amount of carbon in the carbonized layer was 0.73-0.86 wt, 90.

Tempering of the blanks was carried out in a vacuum furnace at a temperature of 1220-12607"C in oil. Tempering - three times at 560"C for one hour each time.

Tests of taps made according to the second class of accuracy, in accordance with GOST 3266-81 and GOST 3449-87, were carried out on a 5АО5 threading machine.

The cutting modes met the requirements of GOST 3449-87:

Cutting speed, m/min. 10

Feed, mm/rev. 1.75"

Cutting length, mm 16

Diameter of the through hole, mm 10.2

Cooling of 595 g of emulsol (ee)

Optimal wear on the back surface, mm 1.0 "

Taps were fastened in a split conical sleeve, the bar with holes was installed in the "E" floating device, which ensures self-installation of the tap along the hole during the cutting process.

Modes of the method of processing a cutting tool made of cemented high-speed steel (options), which are similar to the known processing method (prototype) and the red resistance of the tool processed according to these modes, are given in table. 3, and the results of technical tests are given in table. 4.

High-speed cemented steel of the following chemical composition was used as steel for the manufacture of the tool, processed according to the methods stated (options): C-0.1590; St-3,290;

MU-8,390; Mo-6,090; M-3,690; MP-0.890; 51-1,190; TiI-1,595; Sby-0.1590; Mi-0.495; 5-0.03905; P-0.02590; МБ-0.0590; 21-0.0590; "

B-0.0390; Ce-0.08905; Co-0.390; Re-other.) in c » processing (prototype) and red resistance of the tool processed according to these modes

Mo mode Temperature | Amount of carbon in Temperature Temperature of cementation processing, "C | carburized layer, quenching, "C tempering, "C | at multiple (is) o; weight of tempering, NKSZ "7 ee quenching, 2C | tempering, "C z. Yu 07362111 85018501 CHU001 VO (invented he was in 1001 Vyu0111801pu010505y Yu, CO 31000000 YU6511031 1200

BUT IN PI PO PO PO PO PO PO samples in. інструмента зе 17юю0101018ю010000356000001ню600 во (вв)ввівві вв, дова 16610016 то 5юв2овзовз вв, зє310мю01110011001ю65 05600000 Бвово вва, ва 1 ю 0001 мюб1111о8011010люю0вовеовово во, єв 1зю0100011001009ю01000000061 аю вюво во в во, 25-6 1370 - 1230 0,55 1295 650 оплавлення зразків бо instrument zva ov 00vb 0 vyu01011116000010 to 5yuv2ovzovz vv, 60063 yu00106yu0010yu6b1000000y0000000012yu0000Б5о00vovzovo vo, zv | lyu 0101001002yu01000100600000100lavo00vyu 8060 in vo, yu le |... | yuyu || in |. 1. |в (варіанти), який заявляється, та відомого способу обробки (прототипу) 2 ва1в6000100вя60100000з3в400000000по1мм зв « нн ин ше ни шшшшшш нишни но 30114110 41111 ю 05531056 мя 0000001 в1111111111111оплавлення//1111111111111111111111СМ . . oh, na na ron . "

Cementation of tap blanks was carried out in a laboratory vacuum cementation furnace in a methane or acetylene environment at the temperatures indicated in the table. 3, and pressure from 10 to 400 Pa, with the use of a pulsed feed mode of the carburetor, and with obtaining a given value of the amount of carbon in the carburized layer of the tool. The cementation time was from 0.7 to 3.5 hours to obtain a carbonized layer with a thickness of 2.3-2.5 mm.

Hardening of tool blanks was carried out in a vacuum furnace at a temperature of 1150-12957C (for different modes) in oil. Release was carried out one-, two-, three- and four-times with a duration of one hour each, « 70 at the temperatures specified in the table. 3. -o

The preliminary heat treatment of the tool blanks, tempering, was carried out in a vacuum furnace from the temperatures given in the table. 3. Tempering was carried out in oil. And the release was carried out in a chamber "z" electric furnace, lasting one hour.

Testing of the tool for red resistance was carried out by holding it at a temperature of 6407C

Within four hours followed by hardness measurement. b The stability of the taps was determined according to the modes and methods described above.

Summarizing the results of the tests, it can be noted that the durability of the taps made of (2) tungsten-molybdenum and tungsten cemented high-speed steels, which are claimed, is higher than the durability of the tool made of the known matrix alloy on 10-20905, and the durability of 5r Taps made from cemented high-speed steels, which are declared, with an increased amount of cobalt, higher by 18-24905 than the resistance of the known matrix alloy with an increased amount of cobalt (Table 2). The durability of the tool processed according to the variants of the tool processing method from cemented high-speed steel, which are claimed, is 20-3095 higher than the durability of taps processed according to the known method (Table 4).

A group of claimed inventions, based on theoretical calculations, confirmed by experimental data, can be repeatedly reproduced in production. Therefore, the claimed inventions meet the criterion of "industrial use".

Claims (8)

The formula of the invention is 60th and no 1. A high-speed cemented steel containing carbon, silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanide, sulfur and iron, which is distinguished by the fact that it additionally contains nitrogen, manganese, copper, nickel and phosphorus, and as a lanthanide - cerium with the following ratio of components (wt. 905): b5 Co not more than 0.3 Sg 3.0-50 My 2.5-13.0 Mo 1.0-8.0 Mo 2.0-10.0 Mp 0.1-0.8 8i 01-20 Ti not more than 2.0 Sy not more than 0.3 Mi not more than 0.6 Z not more than 0.035 P not more than 0.035 Mb not more than 0.5 7g not more than 0.1 715 V not more than 0.05 Ce not more than 0.1 Co not more than 3.0 Mo 0 .04-0.6 Ge the rest. 2. A high-speed, cementitious steel containing carbon, silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanide, sulfur and iron, which is distinguished by the fact that it additionally contains manganese, copper, nickel and phosphorus, and as a lanthanide - cerium with the following ratio of components (wt. 90): that Co is no more than 0.3 " Cg 3.0-50 my 2.5-13.0 Mo 1.0-8.0 ee ) Mo 2.0-10.0 Mp 0.1-0.8 Z 8i 01-20 h;E Ti no more than 2.0 Si no more than 0.3 i-oi ЗB Mi no more than 0.6 (se) C no more than 0.035 P no more than 0.035 Mb no more than 0.5 « 7g no more than 0.1 V no more than 0.05 - s Se no more than 0.1 z» Co no more than 3.0 Ge the rest. C. High-speed steel, cemented, containing carbon, silicon, chromium, tungsten, vanadium, Ge) molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanide, sulfur and iron, which differs in that it additionally contains manganese , copper, nickel and phosphorus, and as a lanthanide - cerium with the following ratio of components (wt. 90): Cg» C no more than 03 ve Cg 3.0-50 so M 2.5-13.0 Mo 1.0-8 ,0 Mo no more than 2.0 Mp 0.1-0.8 z» 8i 01-20 Ti no more than 2.0 Si no more than 0, 3 Mi no more than 0.6 60 C no more than 0.035 P no more than 0.035 Mb no more than 0.5 7g no more than 0.1 V no more than 0.05 bo Ce no more than 0.1 So no more than 3.0 He rest. 4. A high-speed cemented steel containing carbon, silicon, chromium, tungsten, vanadium, molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanide, sulfur and iron, which is distinguished by the fact that it additionally contains manganese, copper, nickel and phosphorus, and as a lanthanide - cerium with the following ratio of components (wt. 95): Co no more than 0.3 St 3.0-5.0 M 2.5-13.0 Mo 10-80 Mo 2.0- 10.0 Mp 0.1-0.8 and 0.1-2.0 Ti no more than 2.0 Si no more than 0.3 Mi no more than 0.6 C no more than 0.035 P no more than 0.035 Mb no more than 0, 5 7g no more than 0.1 V no more than 0.05 Se no more than 0.1 So 3.0-12.0 « He the rest. 5. A high-speed, cementitious steel containing carbon, silicon, chromium, tungsten, vanadium, szo molybdenum, cobalt, titanium, zirconium, niobium, boron, lanthanide, sulfur and iron, which is distinguished by the fact that it additionally contains manganese, copper, nickel and phosphorus, and as a lanthanide - cerium with the following ratio of "components (wt. 90): "C not more than 03 I"o) St 3.0-5.0 s M 8.5-20.0 Mo 10 -80 Mo not more than 2.0 Mp 0.1-0.8 "vi 0.1-2.0 Z7Z s Ti not more than 2.0 Sy not more than 0.3 :z" Mi not more than 0.6 Z not more 0.035 P no more than 0.035 Ge») Mb no more than 0.5 7g no more than 0.1 ia B no more than 0.05 s» Se no more than 0.1 Co 3.0-12.0 ve Ge the rest. IR e) b. The method of processing a cutting tool made of high-speed steel that can be cemented, which includes cementing, hardening, tempering, which is distinguished by the fact that cementing is carried out at a temperature of 900-12202C, dv with a carbon potential of the carburizing medium, which provides the carbon content in the carburized layer of the workpiece or the finished tool 0.6-1.5 wt. 956, tempering is carried out from a temperature of Р» 1170-1280"C, and tempering is carried out no more than three times at a temperature of 520-640". 7. The method of processing a cutting tool made of cemented high-speed steel, which includes cementation, hardening and tempering, which is distinguished by the fact that before cementing, the first quenching is carried out at a temperature of 1050-13507C, cementing is carried out at a temperature of 900-1220C, with a carbon potential of the carburizing medium, which provides a carbon content of 0.6-1.5 wt. 95 in the carburized layer of the workpiece or finished tool, the second tempering is carried out at a temperature of 1170-1280"C, and tempering is carried out no more than three times at a temperature of 520-64076. 8. The method of processing a cutting tool made of high-speed steel that can be cemented, which includes 65 Cementation, hardening and tempering, which differs in that, before cementing, the first tempering is carried out at a temperature of 1050-1350" followed by tempering at a temperature of 560-780"C, cementing is carried out at a temperature of 900-12202C, with the carbon potential of the carburizing medium, which ensures obtaining a carbon content of 0.6-1.5 wt in the carburized layer of the workpiece or finished tool. 96, the second tempering is carried out at a temperature of 1170-1280"C, and tempering is carried out no more than three times at a temperature of 520-64076. " with " " (Se) (Se) shi s ;" (22) (22) sh» iz 50 IR e) 60 b5