α/β-sialon having improved sintering activity and high edge strength

Abstract

A sintered molded article includes a ceramic of /-sialon having a grain boundary phase, the grain boundary phase containing at least one hard material formed in situ as an additional phase. A method for the production of the sintered molded article uses at least the following compounds as a starting material: Si.sub.3N.sub.4, AlN, and, if applicable, Al.sub.2O.sub.3, at least one oxide of the rare earths, and at least one oxide of the element titanium.

Claims

1. A sintered molded article comprising a ceramic comprising /-sialon having a grain boundary phase, wherein the grain boundary phase contains at least TiN formed in situ as an additional phase from a starting material comprising 70 to 96 wt.-% Si.sub.3N.sub.4, 3 to 15 wt.-% of at least one oxide of the rare earths and/or Y.sub.2O.sub.3, 1 to 15 wt.-% of an aluminum compound, comprising AlN and, optionally, Al.sub.2O.sub.3 in a weight ratio of AlN:Al.sub.2O.sub.3 greater than 4:1, 0.1 to 3 wt.-% of TiO.sub.2, and CaCO.sub.3, wherein the sum of the starting substances corresponds to 100 wt.-%, wherein the sintered molded article has a final density of at least 99%, wherein in the sintered state, in the interior of the sintered molded article, the proportion of -sialon with reference to the entire sialon phase amounts to 20 to 70 vol.-%, and the proportion of -sialon amounts to 80 to 30 vol.-%, and wherein the surface of the sintered molded article, in the sintered state, amounts to a proportion of -sialon with reference to the entire sialon phase from 55 to 95 vol.-%, and the proportion of -sialon amounts to from 5 to 45 vol.-%.

2. The sintered molded article according to claim 1, wherein the sintered molded article has an edge strength of at least 600 N/mm.

3. The sintered molded article according to claim 1, wherein in the sintered state, in the interior of the sintered article, the proportion of -sialon with reference to the entire sialon phase amounts to 30 to 60 vol.-%, and the proportion of -sialon amounts to 70 to 40 vol.-%.

4. The sintered molded article according to claim 1, wherein the surface of the sintered article, in the sintered state, amounts to a proportion of -sialon with reference to the entire sialon phase from 60 to 90 vol.-%, and the proportion of -sialon amounts to from 10 to 40 vol.-%.

5. The sintered molded article according to claim 1, wherein the surface of the sintered molded article in the sintered state has a proportion of -sialon with reference to the entire sialon phase that is higher by 5 to 65 vol than the proportion of -sialon with reference to the entire sialon phase in the interior of the sintered article.

6. The sintered molded article according to claim 1, wherein the sintered molded article has a Vickers hardness HV10 of at least 10 GPa and/or a crack resistance K.sub.Ic of at least 5 MPa*m.sup.0.5.

7. The sintered molded article according to claim 1, wherein the sintered molded article has an edge strength of at least 680 N/mm.

8. The sintered molded article according to claim 1, wherein the surface of the sintered molded article in the sintered state has a proportion of -sialon with reference to the entire sialon phase that is higher by 10 to 55 vol.-% than the proportion of -sialon with reference to the entire sialon phase in the interior of the sintered article.

9. The sintered molded article according to claim 1, wherein the surface of the sintered molded article in the sintered state has a proportion of -sialon with reference to the entire sialon phase that is higher by 15 to 50 vol.-% than the proportion of -sialon with reference to the entire sialon phase in the interior of the sintered article.

10. The sintered molded article according to claim 1, wherein the sintered molded article has a Vickers hardness HV10 of at least 15 GPa and/or a crack resistance K.sub.Ic of at least 6 MPa*m.sup.0.5.

11. The sintered molded article according to claim 1, wherein starting material comprises 82 to 88 wt.-% Si.sub.3N.sub.4, 8.5 to 13.7 wt.-% of at least one oxide of the rare earths and/or Y.sub.2O.sub.3, 3 to 9.2 wt.-% of an aluminum compound, comprising AlN and, optionally, Al.sub.2O.sub.3, 0.25 to 2 wt.-% of TiO.sub.2, and 0.08 to 0.22 wt.-% CaCO.sub.3.

12. A sintered molded article comprising a ceramic comprising /-sialon having a grain boundary phase, wherein the grain boundary phase contains at least TiN formed in situ as an additional phase by sintering a starting material without pressure or with gas pressure, the starting material comprising 75 to 92 wt.-% Si.sub.3N.sub.4, 3 to 15 wt.-% of at least one oxide of the rare earths and/or Y.sub.2O.sub.3, 1 to 15 wt.-% of an aluminum compound, comprising AlN and, optionally, Al.sub.2O.sub.3 in a weight ratio of AlN:Al.sub.2O.sub.3 greater than 4:1, 0.1 to 3 wt.-% of TiO.sub.2, and CaCO.sub.3, wherein the sum of the starting substances corresponds to 100 wt.-%, wherein the sintered molded article has a final density of at least 99%, wherein in the sintered state, in the interior of the sintered molded article, the proportion of -sialon with reference to the entire sialon phase amounts to 20 to 70 vol.-%, and the proportion of -sialon amounts to 80 to 30 vol.-%, and wherein the surface of the sintered molded article, in the sintered state, amounts to a proportion of -sialon with reference to the entire sialon phase from 55 to 95 vol.-%, and the proportion of -sialon amounts to from 5 to 45 vol.-%.

13. The sintered molded article according to claim 12, wherein the sintered molded article has an edge strength of at least 600 N/mm.

14. The sintered molded article according to claim 12, wherein in the sintered state, in the interior of the sintered article, the proportion of -sialon with reference to the entire sialon phase amounts to 30 to 60 vol.-%, and the proportion of -sialon amounts to 70 to 40 vol.-%.

15. The sintered molded article according to claim 12, wherein the surface of the sintered article, in the sintered state, amounts to a proportion of -sialon with reference to the entire sialon phase from 60 to 90 vol.-%, and the proportion of -sialon amounts to from 10 to 40 vol.-%.

16. The sintered molded article according to claim 12, wherein the surface of the sintered molded article in the sintered state has a proportion of -sialon with reference to the entire sialon phase that is higher by 5 to 65 vol than the proportion of -sialon with reference to the entire sialon phase in the interior of the sintered article.

17. The sintered molded article according to claim 12, wherein the sintered molded article has a Vickers hardness HV10 of at least 10 GPa and/or a crack resistance K.sub.Ic of at least 5 MPa*m.sup.0.5.

18. The sintered molded article according to claim 12, wherein the sintered molded article has an edge strength of at least 680 N/mm.

19. The sintered molded article according to claim 12, wherein the surface of the sintered molded article in the sintered state has a proportion of -sialon with reference to the entire sialon phase that is higher by 10 to 55 vol.-% than the proportion of -sialon with reference to the entire sialon phase in the interior of the sintered article.

20. The sintered molded article according to claim 12, wherein the surface of the sintered molded article in the sintered state has a proportion of -sialon with reference to the entire sialon phase that is higher by 15 to 50 vol.-% than the proportion of -sialon with reference to the entire sialon phase in the interior of the sintered article.

21. The sintered molded article according to claim 12, wherein the sintered molded article has a Vickers hardness HV10 of at least 15 GPa and/or a crack resistance K.sub.Ic of at least 6 MPa*m.sup.0.5.

22. The sintered molded article according to claim 12, wherein starting material comprises 82 to 88 wt.-% Si.sub.3N.sub.4, 8.5 to 13.7 wt.-% of at least one oxide of the rare earths and/or Y.sub.2O.sub.3, 3 to 9.2 wt.-% of an aluminum compound, comprising AlN and, optionally, Al.sub.2O.sub.3, 0.25 to 2 wt.-% of TiO.sub.2, and 0.08 to 0.22 wt.-% CaCO.sub.3.

Description

BRIEF DESCRIPTION OF THE DRAWING

(1) FIG. 1 shows the results of the wear test for a gas-pressure-sintered comparison example A and the embodiments B and C according to the invention.

DETAILED DESCRIPTION OF THE INVENTION

(2) This solution of the task set can, in fact, be evaluated as surprising, because according to Petzow & Herrmann (High Performance Non-Oxide Ceramics II, 47-167 (2002)), sintering additives for sialon ceramics under sintering conditions should be stable oxides that do not lead to the decomposition of Si.sub.3N.sub.4 with the formation of additive nitrides and SiO.sub.2. In this connection, TiO.sub.2 is specifically mentioned as a negative example, see p. 81, for example.

(3) Particularly preferably, the oxides of the element titanium are added in an amount of 0.1 to 3 wt.-%. Especially preferably, TiO.sub.2 is used as a sintering additive.

(4) In a method according to the invention for producing a sintered molded article from /-sialon, having a grain boundary phase that comprises at least one hard material formed in situ, a starting material is used, in addition to the stated sintering additive, which material comprises at least the following compounds: -Si.sub.3N.sub.4, AlN and, if applicable, Al.sub.2O.sub.3, as well as at least one further sintering additive selected from oxygen-containing and/or nitrogen-containing compounds of the elements of the rare earths (lanthanoids without promethium), yttrium, scandium, lithium, beryllium; nitrogen-containing compounds of the elements zirconium and/or hafnium; as well as compounds of the elements magnesium, calcium, strontium. Oxides of the elements ytterbium, erbium, dysprosium, yttrium, scandium, cerium; oxides, hydroxides and/or carbonates of the elements magnesium, calcium, as well as nitrides of the elements zirconium and hafnium are preferred. Oxides of the elements ytterbium, cerium, yttrium and/or carbonates of the elements magnesium and calcium are particularly preferred.

(5) Use of TiO.sub.2 as a sintering additive is surprisingly possible if the addition of the aluminum that is required for sialons essentially takes place in the form of aluminum nitride (AlN), preferably in a weight ratio of AlN:Al.sub.2O.sub.3 greater than 4:1, preferably greater than 10:1, particularly preferably greater than 50:1. Experiments have shown that if the ratio of AlN/Al.sub.2O.sub.3 is less than 4:1, -sialon is not sufficiently stabilized. Furthermore, the oxygen proportion in the grain boundary phase increases, and this has a negative influence on the high-temperature properties of the sintered molded article. The eutectic point in the system is displaced in the direction toward lower temperatures by adding TiO.sub.2 and AlN. A eutectic melt phase forms. This melt phase furthermore makes it possible to reduce the explicit additive content and to nevertheless achieve sufficient compaction even during pressure-free sintering.

(6) Ceramic components that were produced using TiO.sub.2 as a sintering additive demonstrate less warping and better compaction than components that were compacted using conventional sintering additives such as, for example, larger amounts of AlN, CaCO.sub.3 or oxides of the rare earths.

(7) The -Si.sub.3N.sub.4 raw material dissolves in the aforementioned melt phase during the compaction process (sintering). When the solubility limit is exceeded, elongated -sialon needles and globular -sialon grains stabilized by rare earths are formed. In this process, Al.sup.3+ ions of the added AlN are built into the Si.sub.3N.sub.4 crystal lattice in place of the Si.sup.4+ ions. In the case of the -sialon, for reasons of charge neutrality, an N.sup.3 ion must be replaced with an O.sup.2 ion for every Al.sup.3+ that is built in. In the case of the -sialon, in addition to the Al.sup.3+ ions, large cations (generally SEE.sup.3+ ions) are built into the crystal lattice in order to stabilize the -sialon modification. Here, charge equalization also takes place by means of the installation of O.sup.2 ions. By means of this replacement of N.sup.3 with O.sup.2, the concentration of the N.sup.3 ions in the melt is increased and the concentration of the O.sup.2 ions is reduced. Because nitrogen-containing grain boundary phases increase the viscosity and the softening temperature, this leads to increased temperature resistance of the sintered molded articles.

(8) The oxidic titanium sintering additive converts at least in part, preferably by more than 95%, to a nitridic hard material, so that the sintered molded article contains hard materials formed in situ. If, for example, TiO.sub.2 is added as a sintering additive, the hard material TiN forms in the sintered molded article, and TiO.sub.2 can no longer be detected by means of X-ray diffractometry. The remaining sintering aids not built into the sialon crystal structure and/or converted to hard material are present in the sintered molded article in the form of an amorphous and/or partially crystalline grain boundary phase.

(9) A further important property of technical ceramics, particularly in the case of wear applications such as in the case of cutting materials, is the edge strength against spalling R.sub.eA. The edge strength was essentially determined according to Method A of DIN CEN/TS 843-9:2010-11-01. In deviation from DIN CEN/TS 843-9:2010-11-01, for one thing a testing machine having a precision of 2.5% of the displayed force was used, for another thing, the samples were not held in an unchangeable position, using a clamping device, but rather checked while being freely movable, with the exception of an edge stop. Indexable inserts having the geometry SNMX 120716 T02020 were used for determining the edge strength. The indentation for determining the edge strength took place on what is called the cutting surface. The circumference of the indexable inserts was not hard-treated and was therefore in what is called the as fired state. The shortest distance from the circumference of the indexable insert to the indentation of the diamond used, having a Rockwell geometry, was measured using a light microscope after the spalling force was determined. The higher the edge strength, the higher the cutting speed that can be selected at the same cutting depth and the same advance. This particularly holds true for interrupted cutting, because here, the cutting ceramics are repeatedly subjected to stress with regard to edge stability. According to a particularly preferred further development of the invention, the sintered molded article therefore has an edge strength of at least 600 N/mm. Preferably, the edge strength of the sintered molded article according to the invention lies in the range from 650 to 2000 N/mm, particularly preferably in the range from 900 to 1300 N/mm.

(10) A sintered molded article according to the invention can be produced from the following starting substances: 70 to 96 wt.-% Si.sub.3N.sub.4, 3 to 15 wt.-% of at least one oxide of the rare earths or Y.sub.2O.sub.3, 1 to 15 wt.-% of an aluminum compound, comprising AlN and, if applicable, Al.sub.2O.sub.3, as well as 0.1 to 3 wt.-% of a titanium oxide, preferably TiO.sub.2. Further additives are possible, for example hard materials such as TiN, SiC or the like, or further oxidic additives such as MgO, CaCO.sub.3, Li.sub.2O, etc. However, the sum of the starting substances always amounts to 100 wt.-%.

(11) A particularly preferred embodiment of the invention has a starting material composed of 78 to 95 wt.-% Si.sub.3N.sub.4, 2 to 8 wt.-% AlN, 0 to 1.2 wt.-% Al.sub.2O.sub.3, 2.5 to 6.5 wt.-% Y.sub.2O.sub.3 or 3.3 to 12 wt.-% Yb.sub.2O.sub.3 or a corresponding mixture of the two, 0.08 to 0.22 wt.-% CaCO.sub.3 and 0.25 to 2.0 wt.-% TiO.sub.2, wherein the sum of the starting substances amounts to 100 wt.-%.

(12) As already indicated above, green bodies formed from the starting material can be sintered without pressure or under gas pressure. If the green bodies are sintered without pressure, an advantage of the invention consists in that the sintering activity and thereby the final density of the sintered molded article can be increased by adding an oxide of the element titanium, without having to increase the absolute amount of added sintering additives. In this way, the properties of the variants sintered without pressure can be raised to the level of the properties of the gas-pressure-sintered variants, but at far lower costs.

(13) If the green bodies are gas-pressure-sintered, an advantage of the invention lies in that the wear properties, particularly the oxidation resistance of the ceramics at high application temperatures, can be improved. This improvement is possible because lesser amounts of sintering additives are required for compacting the ceramics, and this in turn leads to a reduced amount of oxidation-susceptible grain boundary phase.

(14) Particularly preferably, the sintered molded articles described are used as a cutting tool, particularly as a cutting insert, as a wear component, for example as a welding roll, welding centering pins, components for bearings (roller bearings or ball bearings), components in an exhaust gas system (exhaust gas flaps), valves or exhaust gas turbochargers.

(15) In the following, the invention will be explained in greater detail using an exemplary embodiment in comparison with a conventionally composed sintered molded article.

(16) The starting materials, see Table 1, were mixed and a green molded article was produced. The molded article was sintered without pressure at 1725 C., for approximately 2 hours, under flowing nitrogen.

(17) TABLE-US-00001 TABLE 1 Example A Example B Example C Starting (comparison (according to (according to material example) the invention) the invention) Si.sub.3N.sub.4 (wt.-%) 84-93 82-92 75-88 Al.sub.2O.sub.3 (wt.-%) 0-1.2 0-1.2 0-1.2 AlN (wt.-%) 3-8 3-8 3-8 Er.sub.2O.sub.3 (wt.-%) 0-1.2 Y.sub.2O.sub.3 (wt.-%) 4.5-6.5 0-1.2 Yb.sub.2O.sub.3 (wt.-%) 8.5-12.5 8.5-12.5 CaCO.sub.3 (wt.-%) 0.08-0.22 0.08-0.22 0.08-0.22 TiO.sub.2 (wt.-%) 0.25-2 0.25-2 % of theoretical 96.36-97.13 99.18-99.97 99.34-99.98 density Vickers 5.5 16.6 16.7 Hardness HV10 (GPa) -sialon 77 75 86 proportion of the as fired surface of the sintered molded article (vol.-%) -sialon 64 55 54 proportion in the interior of the sintered molded article (vol.-%) Crack resistance Cannot be evaluated, 6.6 6.5 (Palmquist) K.sub.lc because no cracks (GPa*m.sup.0.5) can be seen due to high residual porosity Edge strength Cannot be evaluated, 1054.97 946.33 R.sub.eA because parts are too (N/mm) porous and warped

(18) The examples according to the invention and the comparison example differ only in their composition, i.e. the materials used. The examples according to the invention have a TiO.sub.2 component; the amounts of the other components were adapted accordingly. Method parameters such as shaping and sintering conditions were otherwise identical in the examples.

(19) In all cases, an /-sialon sintered molded article occurred, having a grain boundary phase that has not only amorphous components but also crystalline components in the X-ray diffractogram. The sintered molded article of the examples according to the invention furthermore also contained TiN grains formed in situ.

(20) With regard to the properties, it was shown that the examples according to the invention have a relative density that is about 3% higher than the comparison example. This high relative density is also demonstrated in the excellent results that are obtained for Vickers hardness HV10 and crack resistance. The Vickers hardness HV10 accordingly amounts to at least 10 GPa, preferably at least 15 GPa. The crack resistance according to Palmquist accordingly amounts to at least 5 MPa*m.sup.0.5, preferably at least 6 MPa*m.sup.0.5, for a sintered molded article according to the invention.

(21) For comparison example A, it was not possible to determine the crack resistance and the edge strength because the crack progression could not be clearly recognized due to the great residual porosity. The experiment regarding edge strength therefore could not be evaluated, since the cutting inserts were too porous and furthermore warped.

(22) In the sintered state of the material, the sialon phase of the sintered article, in the interior, consists of a proportion of -sialon of 10 to 90 vol.-%, preferably 20 to 70 vol.-%, particularly preferably 30 to 60 vol.-%, and a proportion of -sialon of 90 to 10 vol.-%, preferably 80 to 30 vol.-%, particularly preferably 70 to 40 vol.-% -sialon. The proportion of -sialon and -sialon is determined using X-ray diffractometry images (according to Gazzara and Messier, J. Am. Ceram. Soc. Bull. 56 (1977)).

(23) It is known that the composition of the material in the interior of a sintered molded article can be varied by means of the production parameters, such as, for example, by means of the composition of the powder mixture, the sintering conditions in the furnace, the crucible material, the type of gas, the temperature, and the sintering time. A gradient between the surface and the interior of the sintered article can be present in the sintered molded article, so that what is called the as fired surface contains up to 100% -sialon.

(24) The surface of the sintered molded article in the sintered state preferably has a proportion of -sialon with reference to the entire sialon phase from 50 to 100 vol.-%, preferably from 55 to 95 vol.-%, particularly preferably from 60 to 90 vol.-%, and a proportion of -sialon from 0 to 50 vol.-%, preferably from 5 to 45 vol.-%, particularly preferably from 10 to 40 vol.-%.

(25) The surface of the sintered molded article in the sintered state preferably has a proportion of -sialon with reference to the entire sialon phase that is higher by 5 to 65 vol.-%, preferably by 10 to 55 vol.-%, particularly preferably by 15 to 50 vol.-%, than the proportion of -sialon with reference to the entire sialon phase in the interior of the sintered article.

(26) A gradient can form in the sintered molded article under certain conditions if the surface of the sintered article cools faster than the interior or if the surface is changed in terms of its chemical composition by means of reactions with the atmosphere. An -sialon-rich surface leads to a harder outer layer having an impact-resistant core. Thereby the hardness of the sintered molded article can be increased further at the surface, in addition to the hard material formed in situ, without reducing the high edge strength of the sintered blank, which is machined to be planar and chamfered.

(27) The material according to the invention can be coated with known wear-reducing layers such as, for example, Al.sub.2O.sub.3, TiN, TiC or Ti(C,N), and this increases the wear resistance.

(28) The FIGURE shows the results of the wear test for a gas-pressure-sintered comparison example A and the embodiments B and C according to the invention, which were sintered without pressure, as described above. The width of the wear mark is plotted in millimeters as a function of the cutting length in meters during interrupted cutting of gray cast iron (GJL 150). The wear test was carried out at a cutting speed of 1000 m/min, an advance of 0.50 mm/revolution, and a cutting depth of 2 mm.

(29) At the same cutting length, it is found that the embodiments B and C of the invention, which were sintered without pressure, have comparable or even better wear values than the comparison example A.