CN111684088A - Method for producing tool material and tool material - Google Patents
Method for producing tool material and tool material Download PDFInfo
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- CN111684088A CN111684088A CN201980011196.5A CN201980011196A CN111684088A CN 111684088 A CN111684088 A CN 111684088A CN 201980011196 A CN201980011196 A CN 201980011196A CN 111684088 A CN111684088 A CN 111684088A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K26/00—Working by laser beam, e.g. welding, cutting or boring
- B23K26/20—Bonding
- B23K26/21—Bonding by welding
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K26/00—Working by laser beam, e.g. welding, cutting or boring
- B23K26/34—Laser welding for purposes other than joining
- B23K26/342—Build-up welding
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
- B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass
- B23P15/28—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass cutting tools
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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
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
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Abstract
The present invention provides a method for effectively improving other mechanical properties (such as bending stress, toughness, and impact resistance) without significantly impairing the wear resistance and high-temperature softening resistance of a build-up layer formed by a laser cladding method. The present invention also provides a tool material in which a build-up layer of high-speed tool steel having excellent bending stress, toughness, impact resistance, wear resistance, and the like is formed on the outermost surface of a relatively inexpensive metal base. In order to solve the above problem, the present invention provides a method for manufacturing a tool material, comprising: a laser cladding step of supplying high-speed tool steel powder to the surface of the metal base material and irradiating the surface with a laser beam to form a build-up layer; a spheroidizing annealing process, wherein the surfacing layer is subjected to heat treatment at the temperature of 750-880 ℃; a quenching step of quenching the overlay layer subjected to the spheroidizing annealing step; and a tempering step of tempering the build-up layer after the quenching step.
Description
Technical Field
The present invention relates to a method for producing a tool material for forming a weld overlay of high-speed tool steel on a surface of a metal base material by a laser cladding method, and a tool material produced by the production method.
Background
Conventionally, as one of surface treatment techniques, a technique has been known in which a high-hardness material different from a metal base material is deposited on a surface of the metal base material to improve wear resistance and the like of the outermost surface. In this technique, even if the build-up layer on the surface formed using a high-hardness material is worn, the base material can retain its original shape, and therefore, repeated use can be achieved by performing the same build-up process again on the base material. For example, patent document 1 (japanese patent application laid-open No. 2013-176778) discloses a laser cladding (laser cladding) method for forming a high-hardness build-up layer on the surface of a metal base material by a laser as a method for building up a build-up weld.
Here, as a typical high-hardness material used for overlay welding, high-speed tool steel used for high-speed cutting of metal parts and the like can be given. For example, patent document 2 (japanese patent application laid-open No. 2016 and 155155) discloses a technique of depositing a multilayer high-speed tool steel on the surface of a metal base material by a laser cladding method, wherein the deposited layer has hardness and wear resistance equal to or higher than those of a HIP (hot isostatic pressing) material.
Prior art documents
Patent document
Patent document 1: japanese patent laid-open publication No. 2013-176778
Patent document 2: japanese patent laid-open publication No. 2016-155155
Disclosure of Invention
Technical problem to be solved by the invention
However, in conventional overlay welding by the laser cladding method, the overlay welding layer has a rapidly solidified structure, and precipitated carbides segregate at the grain boundaries of the base metal to reduce bending stress, and thus the application thereof is limited. Further, the toughness is lowered in balance with the high hardness, and thus it is difficult to adapt to the use requiring impact resistance.
In view of the problems of the prior art described above, an object of the present invention is to provide a method for effectively improving other mechanical properties (bending stress, toughness, impact resistance, etc.) without significantly impairing the wear resistance, high-temperature softening resistance, etc. of a build-up layer formed by a laser cladding method. Further, an object of the present invention is to provide a tool material in which a build-up layer of high-speed tool steel having excellent bending stress, toughness, impact resistance, wear resistance, and the like is formed on the outermost surface of a relatively inexpensive metal base material.
Means for solving the technical problem
The present inventors have conducted diligent studies on a method for controlling the texture of a high-speed tool steel weld overlay formed by a laser cladding method in order to achieve the above object, and as a result, have found that it is extremely effective to perform heat treatment or the like in an appropriate temperature range, and have completed the present invention.
That is, the present invention provides a method for manufacturing a tool material, comprising:
a laser cladding step of supplying high-speed tool steel powder to the surface of the metal base material and irradiating the surface with a laser beam to form a build-up layer;
a spheroidizing annealing process, wherein the surfacing layer is subjected to heat treatment at the temperature of 750-880 ℃;
a quenching step of quenching the build-up layer subjected to the spheroidizing annealing step; and
and a tempering step of tempering the build-up layer after the quenching step.
The metal structure of the weld overlay formed by the laser cladding method is a rapidly solidified structure, and when high-speed tool steel powder is used as a raw material, precipitated carbides such as tungsten carbide, chromium carbide, vanadium carbide, and molybdenum carbide segregate in a network form at the grain boundaries of the base metal. The segregation of the precipitated carbide lowers the bending stress, toughness, impact resistance, and the like of the weld overlay, but the precipitated carbide can be spheroidized and the network distribution can be split by performing the heat treatment in a temperature range of 750 to 880 ℃.
In the method for manufacturing a tool material according to the present invention, it is preferable that the globularization annealing step includes maintaining the build-up layer at 820 to 880 ℃, cooling the build-up layer to approximately 750 ℃ at a cooling rate of 10 to 50 ℃/hr, and then cooling the build-up layer at a cooling rate of 50 to 150 ℃/hr. In the spheroidizing annealing step, the temperature of the build-up layer is preferably 775 to 825 ℃.
Further, the entire base structure can be made into a pearlite structure by holding the build-up welding layer at 820 to 880 ℃ and then slowly cooling the build-up welding layer to approximately 750 ℃ at a cooling rate of 50 to 150 ℃/hr. Here, it is preferable to keep the temperature at 750 ℃ for about one hour. When the heat treatment temperature is controlled by the furnace temperature, the temperature of the build-up layer (the temperature of the build-up layer) may not be reached even if the furnace temperature is 750 ℃. The final cooling is performed at a cooling rate of 50 to 150 ℃/hr, but the cooling rate can be easily achieved by, for example, furnace cooling.
In the method for producing a tool material according to the present invention, the quenching temperature in the quenching step is preferably 1120 to 1190 ℃. By setting the quenching temperature to this temperature range, sufficient hardness can be imparted to the high-speed tool steel laser weld overlay and toughness can be ensured.
In the method for producing a tool material according to the present invention, the tempering temperature in the tempering step is preferably 540 to 570 ℃, more preferably substantially 560 ℃. When the tempering temperature is set to a temperature (peak temperature) at which the tempering hardness of the build-up layer becomes the highest, the obtained structure becomes unstable, but by tempering at a temperature higher than the peak temperature, a stable structure can be obtained. Further, by repeating the tempering step three or more times, a stable structure can be obtained more reliably.
In the method for manufacturing a tool material according to the present invention, it is preferable that the laser cladding step includes forming two or more of the build-up layers in a thickness direction, and that end portions of adjacent lower and upper build-up layers are not located at the same position. By forming two or more build-up layers in the thickness direction, the total thickness of the build-up layers can be set arbitrarily, and by making the end portions of the adjacent lower and upper build-up layers not be at the same position, the separation of the build-up layers can be suppressed.
Furthermore, the invention also provides a tool material, which is characterized in that,
at least two laser build-up welding layers of high-speed tool steel are formed on the surface of the metal base material along the thickness direction,
the precipitated carbide of the laser weld overlay is substantially spherical and does not segregate at the grain boundaries of the base material.
In the tool material of the present invention, the outermost surface is a laser-welded layer of high-speed tool steel having excellent high-temperature softening resistance and wear resistance, and the precipitated carbides of the laser-welded layer are substantially spherical and do not segregate at the grain boundaries of the base metal, and therefore have high bending stress and impact resistance. That is, the tool material of the present invention can be used for various tools, wear-resistant members, and the like, and can be suitably used for large-sized members because the laser build-up layer can be formed in a wide area. Further, the material cost of the tool material can be reduced by using an inexpensive material as the metal base material, and for example, by using a metal base material having toughness and the like superior to those of the laser build-up layer, the reliability and the like of the entire tool material can be improved.
Here, "the precipitated carbide is substantially spherical" means that the spheroidization progresses more than the precipitated carbide segregated at the grain boundaries of a normal high-speed tool steel weld overlay having a rapidly solidified structure. Further, "the precipitated carbides are not segregated at the grain boundaries of the matrix material" means that the precipitated carbides segregated at the grain boundaries in the normal rapid solidification structure exist not only at the grain boundaries but also within the grains, and the arrangement of the precipitated carbides is split. As a result, the crack can be suppressed from spreading along the precipitated carbide.
The metal base material is not particularly limited as long as the effects of the present invention are not impaired, and various conventionally known metal base materials can be used, but a steel material is preferably used from the viewpoint of adhesion to a laser weld overlay of high-speed tool steel formed on the surface, suppression of dilution, mechanical properties, and the like, and for example, tool steel, bearing steel, and the like can be suitably used.
The region where the high speed tool steel laser weld overlay is formed and the thickness of the high speed tool steel laser weld overlay are not particularly limited, and the high speed tool steel laser weld overlay having an appropriate thickness may be formed only in a necessary region on the surface of the metal base material.
In the tool material according to the present invention, it is preferable that the laser build-up layers include a lower laser build-up layer and an upper laser build-up layer adjacent to each other. By making the positions of the end portions of the lower laser build-up layer and the upper laser build-up layer different, it is possible to suppress peeling of the build-up layers due to application of various stresses, thermal shock, or the like.
In the tool material of the present invention, it is preferable that the bending stress of the laser build-up layer is 2500MPa or more. The tool material of the present invention can be suitably used for applications in which a build-up layer is subjected to a large stress by imparting a bending stress of 2500MPa or more to a laser build-up layer of high-speed tool steel which is inherently excellent in high-temperature softening resistance and wear resistance.
Further, in the tool material of the present invention, it is preferable that the metal base material has a cylindrical shape. By forming the outermost surface of the cylindrical metal base material as a high-speed tool steel laser build-up layer, the tool material of the present invention can be used as a roll, for example.
In the tool material of the present invention, the hardness of the weld overlay is preferably 850HV or more. By setting the hardness of the build-up layer to 850HV or more, the tool material can be used for various cutting tools, wear-resistant members, and the like.
In addition, the tool material of the present invention can be suitably produced by the method for producing a tool material of the present invention.
Effects of the invention
According to the present invention, it is possible to provide a method capable of effectively improving other mechanical properties (bending stress, toughness, impact resistance, etc.) without significantly impairing the wear resistance, high-temperature softening resistance, etc. of a build-up layer formed by a laser cladding method. The present invention also provides a tool material in which a build-up layer of high-speed tool steel having excellent bending stress, toughness, impact resistance, wear resistance, and the like is formed on the outermost surface of a relatively inexpensive metal base.
Drawings
Fig. 1 is a process diagram of a method for producing a tool material of the present invention.
Fig. 2 is a schematic view of the metallic structure of the build-up layer before the heat treatment process.
Fig. 3 is a schematic view of the metallic structure of the build-up layer after the heat treatment process.
Fig. 4 is a schematic cross-sectional view showing an example of the tool material of the present invention.
FIG. 5 is a schematic sectional view of a tool material (hot rolling roll) of the present invention.
Fig. 6 is a schematic cross-sectional view of a tool material (roll for a steel rod or a wire rod) according to the present invention.
FIG. 7 is a schematic sectional view of a tool material (billet or steel sheet roll) according to the present invention.
Figure 8 is a cross-sectional photomicrograph of the implement tool material.
Fig. 9 is a graph showing vickers hardnesses of the build-up layers and sintered bodies obtained in examples and comparative examples.
Fig. 10 is a structural photograph of the build-up layer before the heat treatment of the tool material is performed.
Fig. 11 is a structural photograph of the weld overlay after the heat treatment of the tool material.
Fig. 12 is a graph showing the bending stress (bending strength) of the build-up layer and the sintered body.
Fig. 13 is a graph showing the wear resistance of the build-up layer and the sintered body.
Detailed Description
Hereinafter, a method for manufacturing a tool material and a representative embodiment of the tool material according to the present invention will be described in detail with reference to fig. 1 to 4. However, the present invention is not limited to the drawings, and the drawings are only for conceptually illustrating the present invention, and therefore, in order to facilitate understanding, the scale and the number may be exaggerated or simplified as necessary. In the following description, the same or corresponding portions are denoted by the same reference numerals, and redundant description thereof is omitted.
1. Method for manufacturing tool material
Fig. 1 shows a process diagram of a method for producing a tool material of the present invention. The method for manufacturing a tool material of the present invention includes a laser cladding step (S01), a spheroidizing annealing step (S02), a quenching step (S03), and a tempering step (S04).
(1) Laser cladding process (S01)
The laser cladding step (S01) is a step of forming a build-up layer by supplying high-speed tool steel powder to the surface of the metal base material and irradiating the surface with a laser beam. In addition, although there are a plurality of types of powder having different compositions in part, the powder may be appropriately selected according to the required properties such as wear resistance and toughness.
The laser cladding method used in the method for producing a tool material of the present invention is not particularly limited as long as the effect of the present invention is not impaired, and various conventionally known laser cladding methods can be used. The laser cladding method is a surface treatment method in which a build-up layer is integrally formed on a metal base material by supplying fine metal powder having a uniform particle diameter to a laser irradiation region on the surface of the metal base material, and is also used for manufacturing an intermediate (that is, a tool material) in a manufacturing stage of a cutting tool, a rolling tool, or the like.
In this laser cladding method, the build-up layer is formed by rapid melting and rapid solidification because the metal powder is melted by condensing a laser beam emitted from a laser light source and performing local heat input. In addition, thermal strain and a heat affected zone to the base material can be reduced, and the dilution ratio between the base material and the formed build-up layer can be reduced. Further, since the blowpipe portion (torch) from which the laser beam and the metal powder are emitted can be controlled by a robot by a program, the formation position and the shape of the build-up layer can be controlled relatively accurately, and therefore, the method can be suitably used for repairing cracks or the like appearing on a part of the metal member.
In laser cladding, high-speed tool steel powder having an appropriate composition, particle size distribution, and the like may be used as a raw material, and process conditions may be appropriately adjusted to be optimal according to the size, characteristics, and the like of a build-up layer to be formed, but high-speed tool steel powder having a diameter of 50 to 150 μm is preferably used. Further, the metal base material is not particularly limited as long as the effects of the present invention are not impaired, and various conventionally known metal base materials can be used, but a steel material is preferably used from the viewpoint of adhesion to a high-speed tool steel build-up layer formed on the surface, suppression of dilution, mechanical properties, and the like, and tool steel, bearing steel, and the like can be suitably used. More specifically, for example, a medium carbon steel material (S45C, etc.), a chromium molybdenum steel material, an alloy tool steel material, a high carbon chromium bearing steel material, or the like can be used.
Here, in the laser cladding step (S01), the substantially planar multilayer build-up layer is formed by basically reciprocating the entire body a plurality of times by the linear movement and the parallel movement with a predetermined interval of the laser beam, but the present invention is not limited to this, and for example, the build-up portion may be formed by repeating only the linear movement a predetermined number of times, or the linear movement and the curved movement may be combined, and the combination may be repeated a predetermined number of times.
In the laser cladding step (S01), it is preferable that two or more build-up layers are formed in the thickness direction, and the end portions of the adjacent lower and upper build-up layers are not located at the same position. By forming two or more build-up layers in the thickness direction, the total thickness of the build-up layers can be set arbitrarily, and by making the end portions of the adjacent lower and upper build-up layers not be at the same position, the separation of the build-up layers can be suppressed.
(2) Spheroidizing annealing process (S02)
The spheroidizing annealing step (S02) is a step of applying a heat treatment for spheroidizing and uniformly dispersing precipitated carbides to the build-up layer formed in the laser cladding step (S01).
The metallic structure of the weld overlay formed by the laser cladding process (S01) is a rapidly solidified structure, and when high-speed tool steel powder is used as a raw material, precipitated carbides such as tungsten carbide, chromium carbide, vanadium carbide, and molybdenum carbide segregate in a network form at the grain boundaries of the base metal. The segregation of the precipitated carbide lowers the bending stress, toughness, impact resistance, and the like of the weld overlay, but the precipitated carbide can be spheroidized and the network distribution can be split by performing the heat treatment in a temperature range of 750 to 880 ℃.
In the method for manufacturing a tool material according to the present invention, it is preferable that the globularization annealing step includes maintaining the build-up layer at 820 to 880 ℃, cooling the build-up layer to approximately 750 ℃ at a cooling rate of 10 to 50 ℃/hr, and then cooling the build-up layer at a cooling rate of 50 to 150 ℃/hr. In the spheroidizing annealing step, the temperature of the build-up layer is preferably 775 to 825 ℃.
Fig. 2 and 3 are schematic diagrams showing the metal structure of the build-up layer before and after the spheroidizing annealing step (S02). Before the spheroidizing annealing step (S02), the weld overlay is in a state in which precipitated carbides 4 are segregated in a network form at the grain boundaries of the base material grains 2. Moreover, most of the carbides 4 are analyzed to have a flat shape. On the other hand, by performing the spheroidizing annealing step (S02), the precipitated carbide 4 is dispersed in the crystal grains of the base material crystal grains 2, and the apparent net-like network structure disappears. Further, the shape of the precipitated carbide 4 is changed to a globular shape by the heat treatment.
The distribution and shape change of the precipitated carbide 4 can be effectively obtained by the heat treatment at a temperature ranging from 775 to 825 ℃, and the heat treatment is particularly remarkable in the heat treatment at about 800 ℃. When the temperature of the heat treatment is set to more than 775 ℃ and less than 825 ℃, the precipitated carbide segregated in the form of a network in the grain boundary of the base material can be spheroidized and the network distribution can be split in the microstructure of the high-speed tool steel base material having the rapidly solidified structure. The change in the precipitated carbide can improve toughness, impact resistance, and the like. The present inventors have also found that the temperature range is obtained by examining the heat treatment conditions of the laser weld overlay of high-speed tool steel having a rapidly solidified microstructure in detail.
The heat treatment time in the spheroidizing annealing step (S02) is preferably 30 minutes or longer. By setting the retention time of the heat treatment to 30 minutes or more, the precipitated carbide 4 segregated in a network form can be sufficiently split. As a result, the bending stress, toughness, impact resistance, and the like of the laser weld overlay of high-speed tool steel can be improved. Further, the holding time is more preferably one hour or more, and most preferably three hours or more.
Preferably, the high-speed tool steel laser weld overlay is maintained at 820 to 880 ℃, then cooled to approximately 750 ℃ at a cooling rate of 10 to 50 ℃/hr, and then cooled at a cooling rate of 50 to 150 ℃/hr. In the spheroidizing annealing step, the temperature of the build-up layer is preferably 775 to 825 ℃.
Further, the weld overlay is maintained at 820 to 880 ℃, and then slowly cooled to approximately 750 ℃ at a cooling rate of 50 to 150 ℃/hr, whereby the entire matrix structure can be made into a pearlite (pearlite) structure. Here, it is preferable to keep the temperature at 750 ℃ for about one hour. When the heat treatment temperature is controlled by the furnace temperature, the temperature of the build-up layer (the temperature of the build-up layer) may not be reached even if the furnace temperature is 750 ℃. The final cooling is performed at a cooling rate of 50 to 150 ℃/hr, but the cooling rate can be easily achieved by furnace cooling.
As a heating means for the heat treatment, a heat treatment furnace, a heat treatment bath, or the like can be used, but from the viewpoint of preventing oxidation, it is preferable to perform the heat treatment in an inert gas atmosphere or a reduced pressure/vacuum atmosphere. Further, the entire high-speed tool steel laser weld overlay layer is not necessarily subjected to heat treatment for the purpose of spheroidizing annealing, and for example, when heat treatment is performed locally, laser irradiation, high-frequency induction heating, or the like may be used. By heating by these methods, a laser irradiation apparatus for laser cladding can be used without preparing a large facility such as a heat treatment furnace. Further, the heat treatment can be performed only on a desired region, and the energy consumption amount required for the heat treatment can be reduced. Further, since the position of laser irradiation or high-frequency induction heating can be easily controlled, heat treatment can be easily performed also on a large-sized member such as a roll.
As a specific method of performing the heat treatment by laser irradiation, parameters such as power and focus of the laser beam are adjusted to be optimum so that the region of the build-up layer to be subjected to the heat treatment can be maintained at the predetermined temperature, and then the target region is irradiated with the laser beam for a predetermined time to heat the target region.
In addition, when the entire region of the surface cannot be irradiated with the laser light even if the irradiation range is adjusted to the widest focus setting due to the wide area of the target region, the entire region of the target is scanned by moving the laser irradiation range after adjusting the scanning speed of the laser light to the optimum speed or repeating the movement. In this case, although there is a difference in the amount of input heat between the laser irradiation region and the non-laser irradiation region, the heat treatment conditions can be satisfied by using the scanning speed and the focus setting that can maintain the predetermined temperature over the entire target region.
(3) Quenching step (S03)
The quenching step (S03) is a step of quenching the laser-welded high-speed tool steel layer in which the shape and dispersion of the precipitated carbides 4 have been improved by the spheroidizing annealing step (S02).
The quenching temperature is not particularly limited as long as the effect of the present invention is not impaired, and any conventionally known appropriate temperature may be used for the high-speed tool steel, but the temperature is preferably 1120 to 1190 ℃. By setting the quenching temperature in this temperature range, the hardness of the laser weld overlay of the high-speed tool steel can be sufficiently increased, and the toughness can be ensured.
(4) Tempering process (S04)
The tempering step (S04) is a step for adjusting the hardness of the high-speed tool steel laser weld overlay after the quenching step (S03) is performed, and for stabilizing the structure.
The tempering temperature is not particularly limited as long as the effect of the present invention is not impaired, and any conventionally known appropriate temperature may be used for the high-speed tool steel, but the temperature is preferably 540 to 570 ℃, and more preferably substantially 560 ℃. When the tempering temperature is set to a temperature (peak temperature) at which the tempering hardness of the build-up layer becomes the highest, the obtained structure becomes unstable, but by tempering at a temperature higher than the peak temperature, a stable structure can be obtained. Further, by repeating the tempering step three or more times, a stable structure can be obtained more reliably.
2. Tool material
A schematic cross-sectional view of the tool material of the present invention is shown in fig. 4. The tool material 10 of the present invention is characterized in that a high-speed tool steel laser weld overlay 14 is formed on the surface of a metal base material 12, and precipitated carbides 4 of the high-speed tool steel laser weld overlay 14 are substantially spherical and do not segregate at the grain boundaries of a base material crystal 2.
As shown in fig. 3, the microstructure of the high-speed tool steel laser weld overlay 14 is such that the precipitated carbides 4 are dispersed in the crystal grains of the base material crystal grains 2, and the apparent net-like network structure of the precipitated carbides 4 disappears. The precipitated carbide 4 is further spheroidized, and substantially spherical precipitated carbide 4 is included.
When the precipitated carbide 4 segregates at the grain boundary of the base material grain 2, the bending stress decreases and the cohesion between adjacent base material grains decreases, so that when a crack occurs, the crack progresses along the base material grain boundary, but the dispersion of the precipitated carbide 4 improves the cohesion between adjacent base material grains 2, and therefore the progress of the crack, the separation, and the like can be suppressed.
The bending stress of the high speed tool steel laser weld overlay 14 is preferably 2500MPa or more. The tool material of the present invention can also be used favorably in applications where a weld overlay is subjected to a large stress by imparting a bending stress of 2500MPa or more to the high-speed tool steel laser weld overlay 14 which is inherently excellent in high-temperature softening resistance and wear resistance.
The hardness of the high speed tool steel laser weld overlay 14 is preferably 850HV or greater. By setting the hardness of the build-up layer to 850HV or more, the tool material can be applied to various cutting tools, wear-resistant members, and the like.
Also, the high speed tool steel laser weld overlay 14 is preferably a multilayer weld overlay. The multilayer build-up layer can be formed by, for example, a laser cladding method, and can be obtained by, for example, continuously forming a build-up layer formed by 1-time laser cladding in the horizontal direction and/or the vertical direction. By providing the high speed tool steel laser build-up layer 14 as a multilayer build-up layer, the formation area and thickness can be easily controlled.
In the tool material according to the present invention, it is preferable that the laser build-up layers include a lower laser build-up layer and an upper laser build-up layer adjacent to each other. By making the positions of the end portions of the lower laser build-up layer and the upper laser build-up layer different, it is possible to suppress peeling of the build-up layers due to application of various stresses, thermal shock, or the like.
Further, the metal base material 12 is preferably cylindrical. By forming the high-speed tool steel laser build-up layer 14 on the surface of the cylindrical metal base material 12, the tool material 10 can be preferably used as a roll. In addition, when the high speed tool steel laser build-up layer 14 is damaged, etc., it is also possible to perform a repair by laser cladding.
As a raw material of the high speed tool steel laser build-up layer 14, high speed tool steel powder is used. The high-speed tool steel powder may be a plurality of powders having different compositions, but may be selected appropriately according to the required properties such as wear resistance and toughness. The metal base material 12 is not particularly limited as long as the effects of the present invention are not impaired, and various conventionally known metal base materials can be used, but a steel material is preferably used from the viewpoint of adhesion to the high-speed tool steel laser-clad layer 14 formed on the surface, suppression of dilution, mechanical properties, and the like, and tool steel, bearing steel, and the like can be suitably used. More specifically, for example, a medium carbon steel material (S45C, etc.), a chromium molybdenum steel material, an alloy tool steel material, a high carbon chromium bearing steel material, or the like can be used.
The tool material of the present invention can be applied to cases where the dimensions are too large or economically disadvantageous in the conventional HIP (hot isostatic pressing). Further, for example, by applying a cylindrical tool material having the high-speed tool steel laser build-up layer 14 to a large-sized roll or the like, an extremely economical commercial model can be constructed.
Fig. 5 to 7 show cross-sectional views of representative rolls using the tool material 10. FIG. 5 shows a hot rolling roll, FIG. 6 shows a steel bar or wire rod roll, and FIG. 7 shows a steel slab or steel sheet roll. In each roll, a high-speed tool steel laser build-up layer 14 is formed on the surface of the metal base material 12 in contact with the workpiece, thereby ensuring sufficient bending stress, toughness, impact resistance, and wear resistance.
Further, since the high speed tool steel laser weld overlays 14 are formed only in the desired areas of the surface of these rolls, they are relatively inexpensive, and since the portions where damage, wear, or the like occurs with use are the high speed tool steel laser weld overlays 14, reuse can be achieved by repairing the high speed tool steel laser weld overlays 14 in the areas where damage, wear, or the like occurs. As a result, it is possible to achieve significant energy saving, resource saving, and low environmental load compared to the case of using rolls manufactured by casting.
Here, in the tool material of the present invention, since the high speed tool steel laser weld overlay 14 can be formed in an arbitrary region, the hardness and hardness distribution of the high speed tool steel laser weld overlay 14 can be appropriately adjusted by selecting raw material powder of the high speed tool steel laser weld overlay, or the like. For example, in the high-speed tool steel laser weld overlay 14 of a roll for a bar steel or wire rod shown in fig. 6, the hardness can be adjusted for each region according to the degree of wear caused by the interaction with the workpiece. In general, since the boundary region between the bottom surface and the side surface is significantly worn, it is preferable to set the region to have a higher hardness.
Further, for example, in the roll for billet or slab shown in fig. 7, it is also possible to provide appropriate mechanical properties to each high speed tool steel laser weld overlay by using different raw material powders for each high speed tool steel laser weld overlay 14. Specifically, for example, the hardness of the high speed tool steel laser weld overlay 14 may be sequentially increased or decreased in the direction of extension of the roll axis.
The method for producing a tool material and the tool material of the present invention will be further described below with reference to examples, but the present invention is not limited to these examples.
Examples
< example 1 >
A build-up layer is formed on a base material of SCM440 by laser cladding using powder of high-speed tool steel (JIS-SKH40) having a particle size of 50 to 150 [ mu ] m, and then heat treatment (spheroidizing annealing, quenching, and tempering) is performed on the build-up layer. The laser used was a disk laser (DiskLaser), and the laser cladding conditions were as follows: the laser power was 2kW, the laser spot diameter (focal diameter) was 4.3mm, and the laser moving speed was 0.01 m/s.
The spheroidizing heat treatment is performed in a vacuum furnace (vacuum), and in the spheroidizing heat treatment, after being held at 860 ℃ for three hours, the temperature is decreased to 750 ℃ at a cooling rate of 20 ℃/hour, and after being held at 750 ℃ for one hour, furnace cooling is performed. Next, the vacuum furnace was maintained at 1130 ℃ for 20 minutes under a nitrogen atmosphere of 130Pa, and then, quenching was performed by fan cooling while introducing nitrogen gas. After that, the vacuum furnace was evacuated and maintained at 560 ℃ for two hours, and then tempering in which nitrogen gas was introduced and fan cooling was performed was repeated three times, thereby obtaining a working tool material.
Fig. 8 shows a cross-sectional photomicrograph of the obtained working tool material. The build-up layer of high-speed tool steel was formed on the surface of the base material, and no defects such as peeling or cracking were observed. Also, vickers hardnesses of the build-up layers at 1mm and 2mm from the surface in the cross section shown in fig. 8 were measured, and the obtained results are shown in fig. 9. In the hardness measurement, the load was 100gf, the load time was 10s, and the values shown in fig. 9 are average values measured at 50 points along the horizontal line at each depth.
Fig. 10 and 11 show structure photographs (optical microscope photographs) of the build-up layer before and after the heat treatment (spheroidizing annealing, quenching, and tempering), respectively. As is clear from the figure, the precipitated carbide segregated in a network form at the grain boundaries of the base material before the heat treatment, but the network structure was broken up after the heat treatment, and the precipitated carbide was relatively uniformly distributed. The precipitated carbide becomes fine and becomes spherical.
< comparative example 1 >
A comparative tool material 1 was obtained in the same manner as in example 1, except that the heat treatment was not performed at all. Also, the vickers hardness of the build-up layer was measured in the same manner as in example 1, and the obtained results are shown in fig. 9.
< comparative example 2 >
A comparative tool material 2 was obtained in the same manner as in example 1, except that spheroidizing annealing and quenching were not performed. Also, the vickers hardness of the build-up layer was measured in the same manner as in example 1, and the obtained results are shown in fig. 9.
< comparative example 3 >
A comparative tool material 3 was obtained in the same manner as in example 1, except that spheroidizing annealing and quenching were not performed and the tempering temperature was set to 520 ℃. Also, the vickers hardness of the build-up layer was measured in the same manner as in example 1, and the obtained results are shown in fig. 9.
< comparative example 4 >
A comparative tool material 4 was obtained in the same manner as in example 1, except that spheroidizing annealing and quenching were not performed and the tempering temperature was set to 600 ℃. Also, the vickers hardness of the build-up layer was measured in the same manner as in example 1, and the obtained results are shown in fig. 9.
< comparative example 5 >
A sintered body of high-speed tool steel (JIS-SKH40) powder having a particle size of 250 μm was sintered by HIP (hot isostatic pressing), to obtain a comparative tool material 5. Additionally, as the conditions of the sintered body, at 1240 ℃ and 1000kgf/cm2Held for three hours, thereby obtaining a cylindrical sintered body. Also, vickers hardness of the sintered body was measured in the same manner as in example 1, and the obtained results are shown in fig. 9.
From the vickers hardness shown in fig. 9, the working tool material had a sufficiently high hardness of 850HV or more, which was about the same as that of the HIP sintered body (comparative tool material 5), and was applicable to various tools and wear-resistant members.
The four-point bending test was used to measure the bending stress (bending strength) of the build-up layers of the working tool materials and the comparative tool materials 1 to 4 and the comparative tool material 5. The obtained results are shown in fig. 12. As can be seen from the figure, the build-up layer on which the tool material was applied had a bending stress higher than that of the build-up layers of the comparative tool materials 1 to 4 on which no spheroidizing annealing was applied, and also had a bending stress of the same degree as that of the HIP sintered body (comparative tool material 5). This result shows that by using the method for producing a tool material of the present invention, a high-speed tool steel build-up layer can be formed in any region in a manner similar to that of the HIP sintered material regardless of the shape and size.
The wear resistance of the build-up layers of the working tool materials and the comparative tool materials 1 to 4 and the comparative tool material 5 was evaluated by a block-on-ring wear test. Specifically, rings made of SUJ2 were brought into contact with the build-up layer or the sintered body with a load of 10N, 20N, and 40N, respectively, and the width of the wear mark formed was measured. The number of revolutions of the ring was set to 1000rpm, the test time was set to 600 seconds, and the evaluation was performed under the no-lubrication condition. The obtained results are shown in fig. 13.
From the results shown in fig. 13, it is understood that the build-up layer of the tool material had wear resistance comparable to that of the build-up layers of the comparative tool materials 1 to 4 and the HIP sintered body (comparative tool material 5) that had not been subjected to spheroidizing annealing. This result shows that the weld overlay layer on which the tool material was applied maintained good wear resistance while improving toughness and the like by texture control and hardness adjustment.
Description of the symbols
2-parent metal grains, 4-precipitated carbides, 10-tool materials, 12-metal substrates, 14-high speed tool steel laser weld overlay.
Claims (10)
1. A method for manufacturing a tool material, comprising:
a laser cladding step of supplying high-speed tool steel powder to the surface of the metal base material and irradiating the surface with a laser beam to form a build-up layer;
a spheroidizing annealing process, wherein the surfacing layer is subjected to heat treatment at the temperature of 750-880 ℃;
a quenching step of quenching the build-up layer subjected to the spheroidizing annealing step; and
and a tempering step of tempering the build-up layer after the quenching step.
2. The method for producing a tool material according to claim 1,
in the spheroidizing annealing procedure, the overlaying layer is maintained at 820-880 ℃,
then cooling the mixture to about 750 ℃ at a cooling speed of 10-50 ℃/h,
and then cooling at a cooling rate of 50-150 ℃/h.
3. The method for producing a tool material according to claim 1 or 2,
the quenching temperature of the quenching step is 1120-1190 ℃.
4. The method for manufacturing a tool material according to any one of claims 1 to 3,
the tempering temperature in the tempering step is set to be 540-570 ℃.
5. The method for manufacturing a tool material according to any one of claims 1 to 4,
the tempering process is repeated three times or more.
6. The method for manufacturing a tool material according to any one of claims 1 to 5,
in the laser cladding step, two or more build-up layers are formed in the thickness direction, and the end portions of the adjacent lower and upper build-up layers are not located at the same position.
7. A tool material characterized in that,
at least two laser build-up welding layers of high-speed tool steel are formed on the surface of the metal base material along the thickness direction,
the precipitated carbide of the laser weld overlay is substantially spherical and does not segregate at the grain boundaries of the base material.
8. The tool material of claim 7,
in the laser build-up layers, the end portions of the adjacent lower and upper laser build-up layers are at different positions.
9. The tool material according to claim 7 or 8,
the bending stress of the laser surfacing layer is more than 2500 MPa.
10. The tool material according to any one of claims 7 to 9,
the metal substrate is cylindrical.
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| JP2018-020300 | 2018-02-07 | ||
| JP2018020300A JP7185211B2 (en) | 2018-02-07 | 2018-02-07 | Tool material manufacturing method and tool material |
| PCT/JP2019/004423 WO2019156169A1 (en) | 2018-02-07 | 2019-02-07 | Tool material manufacturing method and tool material |
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| JP (1) | JP7185211B2 (en) |
| CN (1) | CN111684088A (en) |
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| CN110952091B (en) * | 2019-12-24 | 2021-08-20 | 芜湖点金机电科技有限公司 | Machining process of high-temperature wear-resistant guide plate for pipe penetration |
| JP7116935B1 (en) * | 2021-03-12 | 2022-08-12 | 住友電工焼結合金株式会社 | Method for manufacturing mold parts |
| CN114086173B (en) * | 2021-11-04 | 2024-02-09 | 中车工业研究院有限公司 | Additive repairing method for axle |
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| JP2019136799A (en) | 2019-08-22 |
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| TWI666082B (en) | 2019-07-21 |
| WO2019156169A1 (en) | 2019-08-15 |
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