CEMENTED CARBIDE WITH IMPROVED TOUGHNESS

Abstract

A cemented carbide comprises particles including a tungsten carbide (WC) as a main component; a binder phase including cobalt (Co) as a main component; and particles including a carbide or a carbonitride of at least one selected from the group consisting of Group 4a, 5a, and 6a elements, or a solid solution thereof, wherein a cubic phase free layer (CFL), in which the carbide or the carbonitride is not formed, is formed from a surface of the cemented carbide to a depth of 5 μm to 50 μm.

Claims

1. A cemented carbide comprising: particles including a tungsten carbide (WC) as a main component; a binder phase including cobalt (Co) as a main component; and particles including a carbide or a carbonitride of at least one selected from the group consisting of Group 4a, 5a, and 6a elements, or a solid solution thereof, wherein a cubic phase free layer (CFL), in which the carbide or the carbonitride is not formed, is formed from a surface of the cemented carbide to a depth of 5 μm to 50 μm, and when a portion from a center of the CFL to a surface of the CFL is referred to as an upper portion of the CFL, a portion from the center of the CFL to a boundary of a bottom of a base material is referred to as a lower portion of the CFL, and a length of a major axis of a Co structure, in which a ratio of the length of the major axis of the Co structure formed in the CFL to a length of a minor axis thereof is 5 or less, is referred to as a size of the Co structure, a size of a largest Co structure in the lower portion of the CFL is 2 times or less a size of a largest Co structure in the upper portion of the CFL.

2. The cemented carbide of claim 1, wherein a thickness of the CFL is in a range of 10 μm to 30 μm.

3. The cemented carbide of claim 1, further comprising 1.5 wt % to 20 wt % of the carbide or the carbonitride including at least one of tantalum (Ta), niobium (Nb), and titanium (Ti), 4 wt % to 10 wt % of the Co, and the WC as well as unavoidable impurities as a remainder.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0013] FIG. 1 is a micrograph of a cemented carbide according to Example 2 of the invention; and

[0014] FIG. 2 is a micrograph of a cemented carbide according to Comparative Example 2 of the invention.

MODE FOR CARRYING OUT THE INVENTION

[0015] Hereinafter, embodiments of the invention will be described in detail with reference to the accompanying drawings. However, the invention may be embodied in many different forms and should not be construed as being limited to the embodiments set forth herein. Rather, these embodiments are provided so that this description will be thorough and complete, and will fully convey the scope of the invention to those skilled in the art.

[0016] In the invention, the expression “Cubic phase Free Layer (CFL)” denotes a surface region in which a binder phase is rich and a cubic carbide phase is absent from a surface of a base material composed of a cemented carbide sintered body to a predetermined depth.

[0017] Also, the expression “size of Co structure” denotes a length of a major axis of the Co structure excluding a Co structure, in which a ratio of a length of the longest major axis to a length of the shortest minor axis is greater than 5, among the Co structures observed in the CFL. Herein, the reason for the exclusion of the elongated Co structure, in which the ratio of the length of the major axis to the length of the minor axis is greater than 5, is to distinguish the Co structure from an irregular coarse Co structure having a great effect on physical properties of the CFL.

[0018] A cutting tool according to an embodiment of the invention includes a cemented carbide which includes particles including a tungsten carbide (WC) as a main component; a binder phase including cobalt (Co) as a main component; and particles including a carbide or a carbonitride of at least one selected from the group consisting of Group 4a, 5a, and 6a elements, or a solid solution thereof, wherein a cubic phase free layer (CFL), in which the carbide or the carbonitride is not formed, is formed from a surface of the cemented carbide to a depth of 5 μm to 50 μm, and, when a portion from a center of the CFL to a surface of the CFL is referred to as an upper portion of the CFL, a portion from the center of the CFL to a boundary of a bottom of a base material is referred to as a lower portion of the CFL, and a length of a major axis of a Co structure formed in the CFL is referred to as a size of the Co structure, a size of a largest Co structure in the lower portion of the CFL is 2 times or less a size of a largest Co structure in the upper portion of the CFL.

[0019] In a case in which a thickness of the CFL is less than 5 μm, the CFL hardly acts as a toughness reinforcement layer, and, in a case in which the thickness of the CFL is greater than 50 μm, wear resistance is rapidly reduced. Thus, the thickness of the CFL may be in a range of 5 μm to 50 μm, for example, 10 μm to 30 μm.

[0020] The cemented carbide, for example, may include 1.5 wt % to 20 wt % of the carbide or the carbonitride including at least one of tantalum (Ta), niobium (Nb), and titanium (Ti), 4 wt % to 10 wt % of the Co, and the WC as well as unavoidable impurities as a remainder. In a case in which an amount of the carbide or the carbonitride is less than 1.5 wt %, wear resistance is rapidly reduced, and, in a case in which the amount of the carbide or the carbonitride is greater than 20 wt %, welding resistance and chipping resistance are rapidly reduced. Thus, the amount of the carbide or the carbonitride may be in a range of 1.5 wt % to 20 wt %. Also, in a case in which an amount of the Co is less than 4 wt %, since the binder phase is insufficient, a binding force between WC particles is weak to reduce the chipping resistance, and, in a case in which the amount of the Co is greater than 10 wt %, since the binder phase is excessive, the wear resistance is rapidly reduced. Thus, the amount of the Co may be in a range of 4 wt % to 10 wt %.

Example 1

[0021] As a base material of a cutting tool according to Example 1 of the invention, 83 wt % of WC powder, 8 wt % of Co powder, 3 wt % of Ti carbonitride powder, and 6 wt % of niobium (Nb) carbide powder were weighed and mixed, and a cemented carbide was then manufactured by a sintering process.

[0022] The sintering process was performed in such a manner that a dewaxing process was performed by heat-treating at a low temperature of 250° C. for 2 hours, preliminary sintering was performed at 1,200° C. for 1 hour, main sintering was performed at 1,500° C. for 1 hour, cooling was performed at a cooling rate of 13.3° C./min from 1,500° C. to 1,100° C. under a vacuum pressure of 6 mbar, and natural cooling to room temperature was then performed.

[0023] In general, during the cooling from 1,500° C. to 1,100° C., since denitrification occurred, other carbides moved into the base material to form a CFL. Solidification proceeded from a surface at a temperature of 1,100° C. or more, and differences in thickness of the CFL and size of a Co structure occurred depending on the degree to which the carbides moved.

[0024] In Example 1 of the invention, the cooling rate to 1,100° C., as a solidification completion point after the main sintering, was controlled to be fast and the vacuum pressure was simultaneously controlled so as to increase uniformity of the Co structure formed in the CFL.

[0025] A hard film having a multilayer structure was formed by sequentially stacking a 2.5 μm thick TiN layer, a 7 μm thick MT-TiCN layer, a 6 μm thick α-Al.sub.2O.sub.3 layer, and a 1.5 μm thick TiN layer on a surface of an insert, which was prepared by using the cemented carbide thus manufactured as a base material, by a chemical vapor deposition (CVD) method.

Example 2

[0026] As a base material of a cutting tool according to Example 2 of the invention, 87.5 wt % of WC powder, 6.5 wt % of Co powder, 1.8 wt % of Ti carbonitride powder, and 4.2 wt % of Nb carbide powder were weighed and mixed, and a cemented carbide was then manufactured under the same sintering conditions as in Example 1.

[0027] The same hard film as that of Example 1 of the invention was formed on a surface of an insert prepared by using the cemented carbide thus manufactured as a base material.

Example 3

[0028] As a base material of a cutting tool according to Example 3 of the invention, 78.8 wt % of WC powder, 5 wt % of Co powder, 1.2 wt % of Ti carbonitride powder, 6.8 wt % of tantalum (Ta) carbide powder, and 8.2 wt % of Nb carbide powder were weighed and mixed, and a cemented carbide was then manufactured under the same sintering conditions as in Example 1.

[0029] The same hard film as that of Example 1 of the invention was formed on a surface of an insert prepared by using the cemented carbide thus manufactured as a base material.

Comparative Example 1

[0030] As a base material of a cutting tool according to Comparative Example 1, 83 wt % of WC powder, 8 wt % of Co powder, 3 wt % of Ti carbonitride powder, and 6 wt % of Nb carbide powder were weighed and mixed as in the same manner as in Example 1, and a cemented carbide was then manufactured by a sintering process.

[0031] The sintering process was performed in such a manner that a dewaxing process was performed by heat-treating at a low temperature of 250° C. for 2 hours, preliminary sintering was performed at 1,200° C. for 1 hour, main sintering was performed at 1,500° C. for 1 hour, cooling was performed at a cooling rate of 3.3° C./min from 1,500° C. to 1,100° C. under a vacuum pressure of 4 mbar, and natural cooling to room temperature was then performed.

[0032] That is, when compared with Example 1, Comparative Example 1 was the cemented carbide manufactured under different cooling conditions from 1,500° C. to 1,100° C.

[0033] The same hard film as that of Example 1 of the invention was formed on a surface of an insert prepared by using the cemented carbide thus manufactured as a base material.

Comparative Example 2

[0034] As a base material of a cutting tool according to Comparative Example 2, 87.5 wt % of WC powder, 6.5 wt % of Co powder, 1.8 wt % of Ti carbonitride powder, and 4.2 wt % of Nb carbide powder were weighed and mixed, and a cemented carbide was then manufactured under the same sintering conditions as in Comparative Example 1.

[0035] The same hard film as that of Example 1 of the invention was formed on a surface of an insert prepared by using the cemented carbide thus manufactured as a base material.

Comparative Example 3

[0036] As a base material of a cutting tool according to Comparative Example 3, 78.8 wt % of WC powder, 5 wt % of Co powder, 1.2 wt % of Ti carbonitride powder, 6.8 wt % of Ta carbide powder, and 8.2 wt % of Nb carbide powder were weighed and mixed, and a cemented carbide was then manufactured under the same sintering conditions as in Comparative Example 1.

[0037] The same hard film as that of Example 1 of the invention was formed on a surface of an insert prepared by using the cemented carbide thus manufactured as a base material.

[0038] Microstructure

[0039] FIG. 1 is a micrograph of the cemented carbide according to Example 2 of the invention. As illustrated in FIG. 1, other carbide particles having a light gray color were observed at a predetermined depth of the cemented carbide, and a CFL, in which the other carbide particles were not observed, was formed above the other carbide particles.

[0040] The Co structure was a structure having a color close to black which was formed in the “upper portion of the CFL” on a surface side based on the center of the CFL and the “lower portion of the CFL”, wherein, with respect to the cemented carbide according to Example 2 of the invention, an irregularly formed coarse Co structure was hardly observed in the lower portion of the CFL.

[0041] FIG. 2 is a micrograph of the cemented carbide according to Comparative Example 2 of the invention. As illustrated in FIG. 2, with respect to the cemented carbide according to Comparative Example 2, a Co structure formed in the lower portion of the CFL, which is coarser than a Co structure formed in the upper portion of the CFL, was partially observed.

[0042] A thickness of the CFL measured in each of the cemented carbides manufactured according to Examples 1 to 3 of the invention and Comparative Examples 1 to 3 and the results of measuring a ratio of a maximum size of the lower Co structure to a maximum size of the upper Co structure from each micrograph using an image analyzer are presented in Table 1 below.

TABLE-US-00001 TABLE 1 Thickness of CFL Size of Co structure Sample (μm) (lower portion/upper portion) Example 1 32 1.2 Example 2 25 1.2 Example 3 14 1.3 Comparative 32 4 Example 1 Comparative 25 3.4 Example 2 Comparative 14 2.1 Example 3

[0043] As illustrated in Table 1, the thicknesses of the CFLs of Example 1 and Comparative Example 1, in which the amount of Co was large, were formed to be large at 32 microns. In contrast, the thicknesses of the CFLs of Example 2 and Comparative Example 2, in which the amount of Co was intermediate, were 25 μm, and the thicknesses of the CFLs of Example 3 and Comparative Example 3, in which the amount of Co was the smallest, were 14 μm.

[0044] The ratio of the maximum size of the lower Co structure to the maximum size of the upper Co structure formed in the CFL in each of the cemented carbides according to Examples 1 to 3 of the invention was low in a range of 1.2 to 1.3, but the ratio of the maximum size of the lower Co structure to the maximum size of the upper Co structure formed in the CFL in each of the cemented carbides according to Comparative Examples 1 to 3 was in a range of 2.1 to 4 which was greater than two times the above ratio in each of the cemented carbides according to Examples 1 to 3.

[0045] This indicated that an irregularly formed coarse Co structure was formed in the lower portion of the CFL of each of Comparative Examples 1 to 3.

[0046] Results of Machining Performance Evaluation

[0047] In order to investigate effects of the above-described difference in the Co structure on machining performance, machining performance tests for wear resistance and impact resistance of each cutting tool were performed under the following two conditions.

[0048] (1) Alloy Steel Wear Resistance Machining Condition [0049] Machining Method: turning (continuous machining of outer diameter) [0050] Workpiece: SCM440 [0051] Vc (machining speed): 280 mm/min [0052] fn (feed rate): 0.25 mm/min [0053] ap (depth of cut): 2 mm [0054] dry/wet: wet

[0055] (2) Carbon Steel Impact Resistance Machining Condition [0056] Machining Method: turning (interrupted machining of outer diameter) [0057] Workpiece: SM45C-V groove [0058] Vc (machining speed): 300 mm/min [0059] fn (feed rate): 0.3 mm/min [0060] ap (depth of cut): 2 mm [0061] dry/wet: wet

[0062] The results of the machining performance tests performed under the above-described conditions are presented in Table 2 below.

TABLE-US-00002 TABLE 2 Ratio of sizes of CFL Co structures Alloy steel Carbon steel thickness (lower portion/ wear impact Sample (μm) upper portion) resistance resistance Example 1 32 1.2 1,370 mm 360 mm Example 2 25 1.2 1,650 mm 260 mm Example 3 14 1.3 1,980 mm 180 mm Comparative 32 4 1,150 mm 270 mm Example 1 Comparative 25 3.4 1,400 mm 150 mm Example 2 Comparative 14 2.1 1,740 mm 100 mm Example 3

[0063] As illustrated in Table 2, the results of the machining performance tests for wear resistance of the steel showed a general trend that the wear resistance was improved and the impact resistance was reduced as the amount of Co in the cemented carbide was reduced.

[0064] When Example 1 and Comparative Example 1 having the same thickness of the CFL were compared with respect to the evaluation results of wear resistance, Example 1 was 1,370 mm, but Comparative Example 1 was low at 1,150 mm. With respect to the evaluation results of impact resistance, Example 1 was 360 mm, but Comparative Example 1 was 270 mm. Thus, Comparative Example 1 showed significantly degraded characteristics in comparison to Example 1.

[0065] Also, when Example 2 and Comparative Example 2 having the same thickness of the CFL were compared with respect to the evaluation results of wear resistance, Example 2 was 1,650 mm, but Comparative Example 2 was low at 1,400 mm. With respect to the evaluation results of impact resistance, Example 2 was 260 mm, but Comparative Example 2 was low at 150 mm.

[0066] Furthermore, when Example 3 and Comparative Example 3 having the same thickness of the CFL were compared with respect to the evaluation results of wear resistance, Example 3 was 1,980 mm, but Comparative Example 3 was low at 1,740 mm. With respect to the evaluation results of impact resistance, Example 3 was 180 mm, but Comparative Example 3 was very low at 100 mm.

[0067] Form the above results, it was confirmed that, if the cemented carbides had the same thickness of the CFL, the cemented carbide having the Co structure according to the embodiment of the invention may have improved wear resistance and impact resistance in comparison to the cemented carbide which did not have the Co structure according to the embodiment of the invention.