Search Images Maps Play YouTube News Gmail Drive More »
Sign in
Screen reader users: click this link for accessible mode. Accessible mode has the same essential features but works better with your reader.

Patents

  1. Advanced Patent Search
Publication numberUS3380861 A
Publication typeGrant
Publication dateApr 30, 1968
Filing dateMay 5, 1965
Priority dateMay 6, 1964
Also published asDE1219239B
Publication numberUS 3380861 A, US 3380861A, US-A-3380861, US3380861 A, US3380861A
InventorsFrehn Fritz
Original AssigneeDeutsche Edelstahlwerke Ag
Export CitationBiBTeX, EndNote, RefMan
External Links: USPTO, USPTO Assignment, Espacenet
Sintered steel-bonded carbide hard alloys
US 3380861 A
Images(1)
Previous page
Next page
Description  (OCR text may contain errors)

April 30, 1968 F. FREHN 3,

SINTERED STEEL-BONDED CARBIDE HARD ALLOYS Filed May 5, 1965 0123' '.5601'ii' lii'l Hours y Inventor: FR 7-2 fiffl/V United States Patent 5 Claims. of its-12.3

ABSTRACT OF THE DISCLOSURE In sintered steel-bonded carbide hard alloys of the type comprising a steel matrix of steel hardenable by the transformation of austenite containing TiC (or a mixture of TiC with equivalent carbides), the hardness of the sinter is preserved when tempered if the steel matrix contains from 0.5 to 3% of copper.

The invention relates to sintered steel-bonded carbide hard alloys in which a matrix of steel that is hardenable by the transformation of austenite contains the carbide in quantities between 12.5% and 72% by weight, and the carbide is titanum carbide of which up to 50% may be replaced by one or more carbides of metals of Groups IV to VI of the Periodic Table.

The group of steel-bonded titanium carbide hard alloys has been known for some time, but its technological evaluation did not begin until quite recently. The entire group of these particular hard metals can be divided, according to the nature of the steel matrix, into hardenable and non-hardenable alloys which can be used in diverse fields where their different technological properties are useful.

A matrix of the hardenable type is one that can be hardened either by the transformation of austenite, that is to say by the formation of martensite, or by precipitation. This last named group includes known hard metals based on steels with a high titanium and/or tungsten content, which are first solution treated at 1000 C. and then tempered at between 300 and 500 C. when they precipitate a phase rich in titanium and/or tungsten. The reheat stability of these alloys is roughly equal to that of the steel matrix so that generally speaking hard alloys that are hardenable by martensite formation can be used only for the purpose of cold shaping and for the production of abrasion-proof parts, whereas the more reheat-resistant precipitation hardenable alloys can also be machined and hot shaped.

The general composition of the steel-bonded titanium carbide hard metals can be defined as being 12 /2 and 75% by weight of titanium carbide, the remaining matrix consisting of transformation-hardenable or precipitationhardenable steel. Preferably alloys are used containing 27 to 37% by weight of titanium carbide, corresponding to about 40 to 55% by volume of TiC. The steel matrix may be any alloy desired to provide wanted properties. Up to 50% of the titanium carbide tiself may be replaced by other known hard carbides, such as tungsten carbide, vanadium carbide, zirconium carbide, niobium carbide, tantalum carbide, chromium carbide and so forth.

These hard metal alloys are always produced by powder 3,380,861 Patented Apr. 30, 1968 metallurgical techniques. To this end the powdered carbide or carbide mixture is mixed with a likewise powdered matrix alloy, ground down to a grain size below 5;, moulded and then sintered in a vacuum below 10 torr at temperatures between 1200 and 1500 C.

The present invention relates to titanum carbide hard metals of the specified kind consisting of a steel matrix which in virtue of its particular composition is hardenable either by martensite formation or by precipitation. The proposed alloys are characterised inthat the steel matrix which is hardenable by the transformation of austenite contains between 0.5 and 3.0%, of copper.

This particularly useful property of the novel hard metal alloys permits the sintered alloys, after having been hardened by quenching from 950 to 1000 C. in oil, to be reheated for 0.5 to 2 hours, preferably for one hour, for the removal of internal stress at temperatures between 150 and 500 C., preferably at the temperature at which the hard metal alloy is expected to be further processed. The stresses in the workpiece are thus removed and its impact resistance and bending strength further improved.

The known precipitation hardenable matrix alloys differ from alloys composed as proposed by the present invention in that they contain the elements titanium or tungsten for forming the precipitating phases. Both elements are strong carbide formers and they react with excess carbon or carbon liberated by titanium decomposition. It is therefore extremely difiicult in practice to control the degree of hardening.

In the production of sinter steel the use of copper as an age hardening element is as such quite well known. However, in order to produce alloys that can be reheated copper contents exceeding 5% and up to about 30% are provided. an the present context it was ascertained that copper contents in this order of magnitude in steelbonded carbide hard metals are useless and that it is a matter of importance to provide the copper in the specified concentration range.

The carbide hard metals composed as herein proposed are produced by powder metallurgical techniques in the same way as the known materials. The component powders are mixed, ground down to a grain size between 3 and 5a, the powder mixture being then moulded and finally sintered at about 1400 C. for 2 hours in a vacuum below 10'- torr. The sintered mouldings are then cooled to room temperature. After having been annealed at between 700 and 750 C., the hardness of the resultant sintered parts is between 38 and 42 Re. In this condition they can be machined. When they have been hardened the parts have a hardness between and 73 Re.

If the parts that have been thus produced are reheated to temperatures from C. to about 500 C. the hardness due to the martensite gradually diminishes but this is compensated by the increased precipitation. In practice this means that a hardness between 70 and 72 kc is retained up to temperatures of about 500 C.

The appended diagrams illustrate the relationship between high-temperature hardness and working temperature. For comparison purposes the measurements were performed, on the one hand, on a sample consisting of normal steel-bonded titanium carbide hard metal and, on the other hand, on an alloy according to the invention containing 2% Cu. The composition of the examined hard metals is given in Table I.

TABLE I TiC Cr M o 0 Cu Fe Treatment Normal steel bonded titanium carbide hard metal.

Hard metal according to the invention.

As shown in the curve in Diagram 1 the tested samples were heated to temperatures rising in 100 C. steps and held at these temperature levels for 1 to 7 hours when they were recooled to room temperature from each of these temperatures. The hardnesses that were then measured are plotted in Diagram 1. Curve I in this diagram illustrates the change in hardness of a normal steelbonded carbide hard metal, whereas curve 11 is that of a hard metal according to the invention containing 2% Cu. As will be understood from these curves the initial hardnesses of the normal steel-bonded titanium hard metal and of the hard metal according to the invention are alike. The hardness of the hard metal according to the invention remains substantially the same up to 500 C., whereas the hardness of the normal steel-bonded titanium carbide hard metal has already diminished considerably at 150 C. Above 500 C. the hardness of the hard metal according to the invention also begins to decline, but it nevertheless still remains above that of the normal steel-bonded titanium carbide hard metal.

The effect of the copper upon the hardness of a tempered or untempered steel-bonded titanium carbide hard metal of the composition Percent by wt.

TiC 33 Cr 2 Mo 2 C 0.5 Fe Remainder TABLE II Hardness in Hardness in Cu, percent Re annealed Re annealed at 100 C. at 500 C.

The table clearly shows that the hardness declines considerably when the copper content rises to over 3% and that there is then no hardening or age hardening effect. The reason for this may be that although the high copper content reduces the sinter temperature of the alloy and would therefore permit the alloy to be sintered at lower temperatures, the steel matrix nevertheless requires high temperatures for forming the alloy. When the copper content exceeds 5% the sintering temperature would therefore have to be 30 to 50 C. lower to prevent the copper from running out or from evaporating at too high a rate. However, the steel matrix would then not be thoroughly sintered and the formation of the alloy would be incomplete so that no hardening by the transformation of austenite (for instance by martensite formation) nor by copper precipitation when reheating is possible.

Up to 50% of the titanium carbide may be replaced, as previously stated, by one or more other hard carbides.

4 What I claim is: 1. A sintered steel-bonded carbide hard metal alloy of the type having a matrix consisting of a steel hardenable by the transformation of austenite and a carbide content present in quantities of from 12.5% to 72% by weight consisting of titanium carbide, of which up to 50% may be replaced by one or more carbides of metals of Group IV or VI of the Periodic Table, wherein the improvement consists in that the said steel matrix contains 0.5 to 3.0% of copper.

2. A sintered steel-bonded carbide hard metal according to claim 1 in which at least one said hard carbide other than titanium carbide is present in the alloy in a content of up to 36% by weight of the alloy.

3. A method of heat treating a steel-bonded carbide hard metal alloy according to claim 1, in which the alloy is hardened by heating to 950 to 1000 C. and quenching in oil and is reheated one or more times for 0.5 to 2.0 hours, at temperatures between 150 and 500 C.

4. The method according to claim 3, in which said reheating is carried on for about one hour.

5. A method for forming treated, steel-bonded hard carbide alloy molding comprising:

mixing in powdered form (a) a steel matrix alloy of the type which is hardenable by the transformation of austenite to martensite, said steel matrix alloy essentially including between 0.5 percent and 3.0 percent copper; and (b) 12.5 percent to 72 percent, by weight, of at least one metal carbide chosen from the group consisting of titanium carbide and a mixture of metal carbides consisting of titanium carbide and up to 50 percent by weight of at least one other carbide of metals of Group IV to Group VI of the Periodic Table grinding the component powders to a grain size between 3 and 511.;

molding and sintering the powder mixture at about 1400 C. for about 2 hours in a vacuum below about 10* torr;

cooling the sintered molding to room temperature;

annealing the sintered molding at between about 700 and 750 C.;

machining the annealed, sintered molding;

reheating the machined, annealed sintered molding to between 150 C. and about 500 C. for about 0.5 to 2.0 hours.

References Cited UNITED STATES PATENTS 2,683,677 7/1954 Walters et a1. 75-125 X 2,694,626 11/1954 Tanczyn 75125 X 2,828,202 3/1958 Goetzel et al. 75-123 2,868,638 1/1959 Mott 75-125 2,891,858 6/1959 Kegerise et a1. 75-125 3,053,706 9/1962 Gregory et a1. 148-31 3,183,127 5/1965 Gregory et al. 148-31 CHARLES N. LOVELL, Primary Examiner.

Patent Citations
Cited PatentFiling datePublication dateApplicantTitle
US2683677 *Jul 27, 1942Jul 13, 1954Kramer Irvin RMethod of precipitation hardening iron alloys
US2694626 *Aug 25, 1950Nov 16, 1954Armco Steel CorpStainless steels
US2828202 *Oct 8, 1954Mar 25, 1958Sintercast Corp AmericaTitanium tool steel
US2868638 *Feb 9, 1956Jan 13, 1959Cooper Alloy CorpPrecipitation hardenable, corrosion resistant, chromium-nickel stainless steel alloy
US2891858 *Sep 28, 1955Jun 23, 1959Carpenter Steel CoSingle phase austenitic alloy steel
US3053706 *Apr 27, 1959Sep 11, 1962134 Woodworth CorpHeat treatable tool steel of high carbide content
US3183127 *Apr 30, 1963May 11, 1965Chromalloy CorpHeat treatable tool steel of high carbide content
Referenced by
Citing PatentFiling datePublication dateApplicantTitle
US3421950 *Aug 29, 1966Jan 14, 1969Deutsche Edelstahlwerke AgMethod of heat-treating workpieces
US3450511 *Sep 4, 1968Jun 17, 1969Deutsche Edelstahlwerke AgSintered carbide hard alloy
US3450528 *Jul 25, 1968Jun 17, 1969Crucible Steel CorpMethod for producing dispersioned hardenable steel
US3492101 *May 10, 1967Jan 27, 1970Chromalloy American CorpWork-hardenable refractory carbide tool steels
US3653982 *Dec 18, 1969Apr 4, 1972Chromalloy American CorpTemper resistant chromium-containing titanium carbide tool steel
US3715792 *Oct 21, 1970Feb 13, 1973Chromalloy American CorpPowder metallurgy sintered corrosion and wear resistant high chromium refractory carbide alloy
US3771975 *Jul 9, 1971Nov 13, 1973Deutsche Edelstahlwerke AgSinter metal alloy
US3800891 *Apr 18, 1968Apr 2, 1974Hughes Tool CoHardfacing compositions and gage hardfacing on rolling cutter rock bits
US3807970 *Jun 8, 1967Apr 30, 1974Greene CDrill proof plate for safes
US3819364 *Sep 29, 1972Jun 25, 1974Deutsche Edelstahlwerke GmbhWelding hard metal composition
US3942954 *Dec 31, 1970Mar 9, 1976Deutsche Edelstahlwerke AktiengesellschaftSintering steel-bonded carbide hard alloy
US3989554 *Apr 25, 1975Nov 2, 1976Hughes Tool CompanyComposite hardfacing of air hardening steel and particles of tungsten carbide
US4844738 *Oct 16, 1987Jul 4, 1989Mitsubishi Kinzoku Kabushiki KaishaUsed as a sliding part in an internal combustion engine
US5358545 *May 4, 1993Oct 25, 1994Carmet CompanyCorrosion resistant composition for wear products
Classifications
U.S. Classification75/241, 148/514, 419/17, 419/11, 75/246, 419/15, 75/236
International ClassificationC22C33/02, C22C29/06, C22C29/00
Cooperative ClassificationC22C29/00, C22C33/0292, C22C29/067
European ClassificationC22C29/00, C22C29/06M, C22C33/02F4H