Patent Application
20240035125
The present invention relates to sintered cemented carbide compositions and, in particular, to sintered cemented carbide compositions exhibiting enhanced bending strength and enhanced high-temperature properties.
In cemented carbides for metal cutting purposes, the quality of a cemented carbide is often determined by its high temperature properties. Hardness of cemented carbides can be reduced dramatically with increasing temperatures with simultaneous increases in scaling and degradative diffusion processes. Additionally, deformation properties of sintered cemented carbides can change substantially at high temperatures. A basic WC—Co cemented carbide, for example, will feature only about one third of its hardness at 800° C. compared to hardness at room temperature. Additions of TiC and (Ta, Nb)C to the WC—Co cemented carbide can increase hot hardness, but losses in hardness may still exceed fifty percent.
Mechanical properties of cemented carbides are also affected by high temperatures encountered during carbide sintering conditions. Grain growth, for example, is very difficult avoid during sintering and hot isostatic pressing (HIPping) of green compacts. As is well known, excessive grain growth can negatively impact bending strength of the sintered cemented carbide. Therefore, specific metal carbides are added to the green compact as grain growth inhibitors.
The complexity of process sequences in cemented carbide manufacture is still further increased in that both tungsten from the tungsten carbide and metals of the grain growth inhibitors diffuse into the binder phase to form a solid solution. Since the solubility of these metals in the binder increases with temperature, the maximum dissolved concentration at a particular temperature can be exceeded, whereby excessive amounts precipitate out of the binder phase or deposit on the surface of the WC grains. Such deposition, however, impairs wetting of the grains with the binder metal, which in turn results in deterioration of the bending strength. With these current technologies, a careful balance is required between desirable high temperature properties and desirable bending strength.
In view of the foregoing disadvantages, sintered cemented carbides are described herein exhibiting enhanced high temperature properties without dramatic losses in bending strength. In some embodiments, a sintered cemented carbide composition comprises tungsten carbide, a metallic binder phase comprising at least one metal of the iron group, and at least one solid solution carbide phase comprising tantalum (Ta) and molybdenum (Mo), wherein a value of (Mo/Ta) in the sintered cemented carbide composition is from 0.3-100, and the sintered cemented carbide composition has a transverse rupture strength of at least 4000 MPa.
In another aspect, a sintered cemented carbide composition comprises tungsten carbide, a metallic binder phase comprising at least one metal of the iron group, and at least one solid solution carbide phase comprising tantalum, molybdenum, and vanadium, wherein tantalum is present in an amount exceeding the solubility limit of tantalum in the metallic binder phase.
In preferred embodiments, vanadium is present in an amount less than tantalum,
In some embodiments, the sintered cemented carbide composition further comprises chromium. In preferred embodiments, the solid solution carbide phase further comprises chromium. Preferably chromium is present in an amount less than tantalum.
In further preferred embodiments, molybdenum is present in an amount of 0.5-3 wt. % of the sintered cemented carbide composition, preferably 0.5 to 2.5 wt. %.
These and other embodiments are further described in the following detailed description.
Embodiments described herein can be understood more readily by reference to the following detailed description and examples and their previous and following descriptions. Elements, apparatus and methods described herein, however, are not limited to the specific embodiments presented in the detailed description and examples. It should be recognized that these embodiments are merely illustrative of the principles of the present invention. Numerous modifications and adaptations will be readily apparent to those of skill in the art without departing from the spirit and scope of the invention.
In one aspect, a sintered cemented carbide composition comprises tungsten carbide, a metallic binder phase comprising at least one metal of the iron group, and at least one solid solution carbide phase comprising tantalum (Ta) and molybdenum (Mo), wherein a value of (Mo/Ta) in the sintered cemented carbide composition is from 0.3-100, and the sintered cemented carbide composition has a transverse rupture strength of at least 4000 MPa.
Turning now to specific components, sintered cemented carbide compositions described herein comprise tungsten carbide (WC). Tungsten carbide of the sintered composition can exhibit any average grain size consistent with the objectives of the present invention. In some embodiments, for example, tungsten carbide grains have an average size of 0.1 μm to 5 μm. Tungsten carbide grains can also have an average size selected from Table I.
Grain size can be determined according to the linear intercept measure. As detailed further herein, tungsten carbide constitutes the balance of the sintered cemented carbide compositions.
Sintered cemented carbide compositions also comprise a metallic binder phase comprising at least one metal of the iron group. In some embodiments, the metallic binder phase is cobalt-based alloy or solely cobalt. The metallic binder phase can be present in any desired amount. The metallic binder phase can generally be present in an amount of 1 weight percent to 30 weight percent of the sintered cemented carbide composition. Metallic binder phase may also be present in the sintered cemented carbide in an amount selected from Table II.
In addition to tungsten carbide and the metallic binder phase, the sintered cemented carbide comprises at least one solid solution carbide phase comprising tantalum (Ta) and molybdenum (Mo), wherein a value of (Mo/Ta) in the sintered cemented carbide is from 0.3-100. In some embodiments, the value of (Mo/Ta) is from 1 to 10 or from 1 to 5. Additional (Mo/Ta) values for the sintered cemented carbide composition can be selected from Table III.
In relation to the Mo/Ta value, Mo can generally be present in the sintered cemented carbide composition in an amount of 0.5 to 5 weight percent. In some embodiments, Mo is present in the sintered cemented carbide in an amount selected from Table IV.
Similarly, in relation to the Mo/Ta value, Ta can generally be present in the sintered cemented carbide in an amount of 0.05 to 1.5 weight percent. In some embodiments, Ta is present in amount exceeding the solubility limit of Ta in the metallic binder phase. Weight percent of Ta in the sintered cemented carbide can also be selected from Table V.
In some embodiments, the solid solution carbide phase can comprise elements in addition to Ta and Mo. The solid solution phase, for example, can further comprise W to provide a (Ta, Mo, W)C solid solution phase.
Moreover, sintered cemented carbide compositions described herein can exhibit high hardness and desirable bending strengths. Applicant has made the discovery that adding molybdenum to the sintered cemented carbide composition can mitigate losses to bending strength induced by increases in tantalum, such as TaC or (Ta, Nb)C, for limiting grain growth and improving hot hardness. Accordingly, sintered cemented carbide compositions described herein can exhibit fine grain structure and high hardness without concomitant losses in bending strength. The sintered cemented carbide compositions exhibit a transverse rupture strength (TRS) of at least 4000 MPa or at least 4500 MPa. In some embodiments, a sintered cemented carbide composition has a transverse rupture strength of 4300 to 4800 MPa. Sintered cemented carbide compositions described herein may also have a transverse rupture strength greater than 4800 MPa. Transverse rupture strength for sintered cemented carbides is determined according to International Organization for Standardization (ISO) 3327:2009. In addition to the foregoing TRS values, sintered cemented carbide compositions described herein exhibit high hardness. A sintered cemented carbide composition, for example, can have hardness of at least 1500 HV30. In some embodiments, a sintered cemented carbide composition has hardness of 1600-2000 HV30. Hardness values are determined according to ASTM E384-17, Standard Test Method for Microindentation Hardness for Materials.
Sintered cemented carbide compositions described here may further comprise chromium. Chromium can generally be present in the sintered cemented carbide composition in an amount of 0.05 to 0.5 weight percent. While increasing hardness, chromium in excess of 0.5 weight percent can result in substantial reductions in transverse rupture strength. In some embodiments, for example, chromium is present in the sintered cemented carbide in an amount less than the tantalum. Alternatively, chromium can be present in the sintered cemented carbide in an amount greater than the tantalum. Additionally, chromium can be incorporated into the solid solution carbide phase comprising Ta and Mo.
Sintered cemented carbide compositions described herein may further comprise vanadium. Vanadium, for example, can be present along with Ta and Mo. In other embodiments, vanadium is present with Ta, Mo, and Cr. Vanadium can generally be present in the sintered cemented carbide composition in an amount of 0.05 weight percent to 0.15 weight percent. For example, vanadium can be present in the sintered cemented carbide composition in an amount of 0.05 to 0.10 wt. % or 0.10 to 0.15 wt. %. In some embodiments, vanadium is present in an amount less than tantalum (V/Ta<1). When present, vanadium may be incorporated into the solid solution phase, such as (V, Ta, Mo)C or (V, Ta, Mo, Cr)C. Tungsten, in some embodiments, can be incorporated into any of the solid solution carbide phases described herein.
The solid solution carbide phase comprising Ta and Mo and, optionally, one or more of V, Cr and W, can precipitate as clusters in the sintered cemented carbide, in some embodiments. Clusters of the solid solution carbide phase can exhibit regular and/or irregular geometries.
Precipitated solid solution carbide clusters can be randomly distributed throughout the sintered cemented carbide. Additionally, precipitated solid solution clusters can display differing sizes. Generally, solid solution carbide clusters have at least one dimension of 5 μm or more. In some embodiments, diameter of a precipitated solid solution cluster is at least 5 μm. A solid solution carbide cluster may have more than one dimension measuring at least 5 μm.
In another aspect, a sintered cemented carbide composition comprises tungsten carbide, a metallic binder phase comprising at least one metal of the iron group, and at least one solid solution carbide phase comprising tantalum, molybdenum, and vanadium, wherein tantalum is present in an amount exceeding the solubility limit of tantalum in the metallic binder phase. In some embodiments, vanadium is present in the sintered cemented carbide composition in an amount less than the tantalum, (V/Ta)<1. Additionally, the solid solution carbide phase may further comprise chromium and/or tungsten, in some embodiments. In some embodiments, chromium is present in an amount greater than vanadium. Tungsten carbide and the metallic binder phase of the sintered composition can have any properties described herein, including those provided in Tables I and II above. Similarly, molybdenum and vanadium can be present in the sintered cemented carbide composition in amounts selected from Table IV and V above. In some embodiments, chromium is optionally present in an amount of 0.05 to 0.5 weight percent.
As described herein, the solid solution carbide phase comprising tantalum, molybdenum, and vanadium can precipitate as one or more clusters. The solid solution clusters can have any of the properties and dimensions described above. Moreover, sintered cemented carbide compositions comprising at least one solid solution carbide phase including tantalum, molybdenum, and vanadium can exhibit any TRS and/or hardness values described above. In some embodiments, for example, the sintered cemented carbide has TRS of at least 4000 MPa or at least 4500 MPa and hardness of at least 1500 HV30.
Sintered cemented carbide compositions described herein, in some embodiments, exhibit magnetic saturation of 75-85% or 75-80%. Magnetic saturation values recited herein are based on magnetic component(s) of the metallic binder phase and are determined according to ASTM B 886-12, “Standard Test Method for Determination of Magnetic Saturation (MS) of Cemented Carbides,” ASTM International. As known to one of skill in the art, magnetic saturation values may be converted from percentages to μTm3/kg or other comparable units based on comparison to a nominally pure Co binder phase. For example, see Roebuck, B. Magnetic Moment (Saturation) Measurements on Hardmetals, Int. J. Refractory Metals & Hard Materials, 14 (1996) 419-424. Additionally, sintered cemented carbide compositions described herein can be free of eta phase and/or other lower carbides, such as W2C.
Sintered cemented carbide compositions described herein can be prepared by providing powdery starting materials including WC as the main constituent, metallic binder, and compounds of Ta and Mo as well as, optionally, compounds of Cr and/or V and milling the starting materials in a ball mill or attrition mill with the addition of carbon or tungsten and/or sintering aids to provide a grade powder. Compounds of Ta, Mo, Cr and/or V can include carbides and/or oxides of these elements. In some embodiments, one or more of Ta, Mo, Cr and V can be added as metal powder. The grade powder is formed into a green article, and the green article is vacuumed sintered or sintered-hot isostatic press (HIP) at a temperature ranging from 1350° C. to 1560° C. for a time period sufficient to produce the sintered cemented carbide of desired density and microstructure.
Sintered cemented carbides described herein can be employed in various applications including, but not limited to, cutting tools. In some embodiments, sintered cemented carbide compositions are formed into cutting inserts, such as indexable turning inserts and interrupted cutting inserts. The sintered cemented carbide compositions can also be formed into rotary cutting tools including drills and endmills of various geometries. In some embodiments, sintered cemented carbide articles having composition and properties described herein are coated with one or more refractory materials by PVD and/or CVD. In some embodiments, the refractory coating comprises one or more metallic elements selected from aluminum and metallic elements of Groups IVB, VB and VIB of the Periodic Table and one or more non-metallic elements selected from Groups IIIA, IVA, VA and VIA of the Periodic Table. For example, the refractory coating can comprise one or more carbides, nitrides, carbonitrides, oxides or borides of one or more metallic elements selected from aluminum and Groups IVB, VB and VIB of the Periodic Table. Additionally, the coating can be single-layer or multi-layer.
These and other embodiments are further illustrated by the following non-limiting examples.
Sintered cemented carbide articles having the compositions set forth in Table VI were produced as follows. Grade powder having the desired compositional parameters of each sample in Table VI was compacted into a green article having shape and dimensions required by ISO 3327:2009. The green article was pressure sintered at peak temperature of 1400° C. to provide the sintered cemented carbide article for TRS and hardness testing. Ta, Mo, V and Cr were employed in grade powders of the relevant samples as TaC, Mo2C, VC, and Cr3C2 respectively. Comparative samples were also prepared where Mo was absent from the composition.
From the results of Samples 2-4 relative to comparative Sample 1, it is clearly seen that the addition of molybdenum increases hardness and TRS for a constant Ta content. Additionally, Samples 6-7 and 10-11 demonstrate that Mo can offset reductions to bending strength (TRS) conventionally induced by increased Ta content. Accordingly, higher amounts of Ta can be used to inhibit grain growth and increase hardness without degrading bending strength.
Samples 11-13 illustrate synergistic effects of adding small quantities of vanadium to the sintered cemented carbide compositions. In particular, the addition of vanadium in conjunction with small amounts of Cr provide the sintered cemented carbide composition with excellent hardness and TRS. Moreover, increased amounts of vanadium can drive precipitation of larger solid solution clusters.
Various embodiments of the invention have been described in fulfillment of the various objects of the invention. It should be recognized that these embodiments are merely illustrative of the principles of the present invention. Numerous modifications and adaptations thereof will be readily apparent to those skilled in the art without departing from the spirit and scope of the invention.
| Number | Date | Country | Kind |
|---|---|---|---|
| 102019110950.7 | Apr 2019 | DE | national |
The present application is a continuation of U.S. patent application Ser. No. 16/859,254, filed on Apr. 27, 2020, which claims priority pursuant to 35 U.S.C. § 119(a) to German Patent Application Number 102019110950.7, filed on Apr. 29, 2019. Both U.S. patent application Ser. No. 16/859,254 and German Patent Application Number 102019110950.7 are incorporated herein by reference in their entirety.
| Number | Date | Country | |
|---|---|---|---|
| Parent | 16859254 | Apr 2020 | US |
| Child | 18379825 | US |
