Corrosion resistant, high vanadium, powder metallurgy tool steel articles with improved metal to metal wear resistance and a method for producing the same

Abstract

A high vanadium, powder metallurgy cold work tool steel article and method for production. The nickel, chromium, vanadium, and carbon plus nitrogen contents of the steel are controlled during production to achieve a desired combination of corrosion resistance, metal to metal wear resistance, and hardenability.

Description

BACKGROUND OF THE INVENTION

1. Field of the Invention

The invention relates to highly wear and corrosion resistant, powder metallurgy tool steel articles and to a method for their production by compaction of nitrogen atomized, prealloyed high vanadium powder particles. The articles are characterized by exceptionally high metal to metal wear resistance, which in combination with their good abrasive wear resistance and corrosion resistance, makes them particularly useful in machinery used for processing reinforced plastics and other abrasive or corrosive materials.

2. Background of the Invention

Basically, there are three types of wear that can occur, often in combination, in the barrels, screws, valves, molds, and other components used in processing reinforced plastics and other aggressive materials. They include metal to metal wear caused in areas where the metal components come into direct contact during operation, abrasive wear caused by continued contact at high pressures of the components with hard particles in the process media, and corrosive wear caused by acids or other corrodents either originally present or released from the process media at elevated temperatures of operation. To perform satisfactorily, the articles used in processing these materials must be highly resistant to these forms of wear. In addition, they must possess sufficient mechanical strength and toughness to withstand the stresses imposed during operation. Further, they must be readily machined, heat treated, and ground to facilitate the manufacture of parts with the required shape and dimensions.

A wide range of materials have been evaluated for the construction of the components employed in the processing of reinforced plastics and other abrasive or corrosive materials. They include chromium plated alloy steels, conventional high chromium martensitic stainless steels such as AISI Types 440B and 440C stainless steels, and a number of high chromium martensitic stainless steels produced by powder metallurgical methods. The compositions of this latter group of materials are broadly similar to those of the conventional high chromium martensitic stainless steels, except that greater than customary amounts of vanadium and carbon are added to improve their wear resistance. The high chromium, high vanadium, powder metallurgy stainless steels, such as CPM 440V disclosed on page 781 in Volume 1 of the 10th Edition of the ASM Metals Handbook and MPL-1 disclosed in recent publications, clearly outperform conventional steels in plastic processing, but none of these materials fully meet all the needs of the newer plastic processing machinery which cannot accommodate large wear related changes in the geometry of the operating parts and where contamination of the process media by wear debris must be minimized. Of all the required properties, the metal to metal wear resistance of the high chromium martensitic stainless steels made either by conventional or powder metallurgy methods is remarkably low.

SUMMARY OF THE INVENTION

It has been discovered in this regard, that the metal to metal wear resistance of the high chromium, high vanadium, powder metallurgical stainless steels is markedly affected by their chromium content and that by lowering their chromium content and closely balancing their overall composition, a significantly improved and unique combination of metal to metal, abrasive, and corrosive wear resistance can be achieved in these materials. In addition, it has been discovered that for some applications the corrosion resistance of these materials can be notably improved by increasing the nitrogen content of the prealloyed powders from which they are made. In addition, it has also been discovered that the hardenability of these materials can be significantly improved by increasing their nickel content. Further, it has been discovered that to obtain the desired combinations of wear and corrosion resistance along with good strength, toughness, and grindability in the articles of the invention, it is necessary to closely control the atomization and compaction conditions of the prealloyed powders from which these improved articles are produced.

It is accordingly a primary object of the invention to provide corrosion resistant, high vanadium, powder metallurgy tool steel articles with notably improved metal to metal wear resistance. This is achieved by closely controlling chromium content, which generally improves corrosion resistance, but which unexpectedly has been found to have a highly negative effect on metal to metal wear resistance, and by balancing the overall composition of the articles so as to obtain the desired degree of hardness and wear resistance without reducing corrosion resistance.

An additional objective of the invention is to provide corrosion resistant, high vanadium, powder metallurgy tool steel articles with notably improved metal to metal wear resistance in which greater than residual amounts of nitrogen are incorporated to improve corrosion resistance without reducing wear resistance.

An additional objective of the invention is to provide corrosion resistant, high vanadium, powder metallurgy tool steel articles with notably improved metal to metal wear resistance in which greater than residual amounts of nickel are incorporated to improve their hardenability.

A still further objective of the invention is to provide a method for producing the corrosion resistant, high vanadium, tool steel articles of the invention with good strength, toughness, and grindability from nitrogen atomized, prealloyed powder particles. This is largely achieved by closely controlling the size of chromium-rich and vanadium-rich carbides or carbonitrides formed during the atomization and hot isostatic compaction of the nitrogen atomized powders from which the articles of the invention are made.

These and other objects of the invention are achieved with powder metallurgical articles in accordance with the following processing and compositions.

In accordance with the method of the invention, the article thereof is produced by nitrogen gas atomizing a molten tool steel alloy at a temperature of 2800 to 3000.degree. F., preferably 2840 to 2880.degree. F., rapidly cooling the resulting powder to ambient temperature, screening the powder to about -16 mesh (U.S. Standard), hot isostatically compacting the powder at a temperature of 2000 to 2100.degree. F. at a pressure of 13 to 16 ksi, preferably 15 ksi, whereby the resulting articles after hot working, annealing and hardening to 58 HRC, have a volume fraction of primary M.sub.7 C.sub.3 and MC carbides of 16 to 36% in which the volume of MC carbides is at least one-third of the primary carbide volume and where the maximum sizes of the primary carbides do not exceed about six microns in their largest dimension and wherein a metal to metal wear resistance of at least 10.times.10.sup.10 psi, as defined herein, is achieved.

__________________________________________________________________________ Preferred Most Preferred Preferred Range Most Preferred Range for Range for for Highest Range for Highest Broad Highest Wear Highest Wear Corrosion CorrosionElement Range Resistance Resistance Resistance Resistance__________________________________________________________________________Carbon* 1.47-3.77 1.83-3.77 2.54-3.77 1.60-3.62 2.31-3.62Manganese 0.2-2.0 0.2-1.0 0.2-1.0 0.2-1.0 0.2-1.0Phosphorus 0.10 max 0.05 max 0.05 max 0.05 max 0.05 maxSulfur 0.10 max 0.03 max 0.03 max 0.03 max 0.03 maxSilicon 2.0 max 0.2-1.0 0.2-1.0 0.2-1.0 0.2-1.0Chromium 11.5-14.5 12.5-14.5 12.5-14.5 12.5-14.5 12.5-14.5Molybdenum 3.0 max 0.5-3.0 0.5-3.0 0.5-3.0 0.5-3.0Vanadium 8.0-15.0 8.0-15.0 12.0-15.0 8.0-15.0 12.0-15.0Nitrogen* 0.03-0.46 0.03-0.19 0.03-0.19 0.20-0.46 0.20-0.46Iron** Balance Balance Balance Balance Balance__________________________________________________________________________ *(% C + 6/7% N).sub.minimum = 0.40 + 0.099 (% Cr - 11.0) + 0.063 (% Mo) + 0.177 (% V); (% C + 6/7% N).sub.maximum = 0.60 + 0.099 (% Cr - 11.0) + 0.063 (% Mo) + 0.177 (% V) **Includes incidental elements and impurities characteristic of steel making practice.

In accordance with the present invention, the above-recited composition ranges are modified by alloying additions of nickel within the ranges of 0.20 to 2.00%, 0.20 to 0.90%, and 0.20 to 0.60%.

It is important in regard to the invention to balance the amount of carbon, nitrogen, and other austenite forming elements in the articles with respect to the ferrite forming elements, such as silicon, chromium, vanadium, and molybdenum, to avoid the formation of ferrite in the microstructure. Ferrite reduces the hot workability of the articles of the invention and lowers their attainable hardness. It is also important to control the amounts of carbon, nitrogen, and other alloying elements in the articles of the invention to avoid forming unduly large amounts of retained austenite during heat treatment as well as to obtain the improved combination of metal to metal, abrasive, and corrosive wear resistance. Specifically, carbon is required within the indicated ranges for controlling ferrite, forming hard wear resistant carbides or carbonitrides with vanadium, chromium, and molybdenum, and for increasing the hardness of the martensite in the matrix. Amounts of carbon greater than the indicated limit reduce corrosion resistance significantly.

The alloying effects of nitrogen in the articles of the invention are somewhat similar to those of carbon. Nitrogen increases the hardness of martensite and can form hard nitrides and carbonitrides with carbon, chromium, molybdenum, and vanadium that can increase wear resistance. However, nitrogen is not as effective for this purpose as carbon in high vanadium steels because the hardnesses of vanadium nitride or carbonitride are significantly less than that of vanadium carbide. In contrast to carbon, nitrogen is useful for improving the corrosion resistance of the articles of the invention when dissolved in the matrix. For this reason, nitrogen in an amount up to about 0.46% can be used to improve the corrosion resistance of the articles of the invention. However, for highest wear resistance, nitrogen is best limited to about 0.19% or to the residual amounts introduced during nitrogen atomization of the powders from which the articles of the invention are made.

To obtain the hardness and carbide or carbonitride volumes needed to achieve the desired combination of wear and corrosion resistance, the carbon and nitrogen in the articles of the invention must be balanced with the chromium, molybdenum, and vanadium contents of the articles according to the following formulas:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V); (%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V)

It is essential in accordance with the invention to control the amounts of chromium, molybdenum, and vanadium within the above indicated ranges to obtain the desired combination of wear and corrosion resistance, along with adequate hardenability, hardness, toughness, machinability, and grindability.

Vanadium is very important for increasing metal to metal and abrasive wear resistance through the formation of MC-type vanadium-rich carbides or carbonitrides in amounts greater than previously obtainable in corrosion and wear resistant powder metallurgy tool steel articles.

Manganese is present to improve hardenability and is useful for controlling the negative effects of sulfur on hot workability through the formation of manganese sulfide. It is also useful for increasing the liquid solubility of nitrogen in the melting and atomization of the high nitrogen powder metallurgy articles of the invention. However, excessive amounts of manganese can lead to the formation of unduly large amounts of retained austenite during heat treatment and increase the difficulty of annealing the articles of the invention to the low hardnesses needed for good machinability.

Silicon is used for deoxidation purposes during the melting of the prealloyed materials from which the nitrogen atomized powders used in the articles of the invention are made. It is also useful for improving the tempering resistance of the articles of the invention. However, excessive amounts of silicon decrease toughness and unduly increase the amount of carbon or nitrogen needed to prevent the formation of ferrite in the microstructure of the powder metallurgical articles of the invention.

Nickel, in amounts up to about 2.00%, has been found to increase the hardenability of the articles of the invention to much greater extent than expected from its reported effects on the hardenability of low alloy steels. Consequently, as with manganese, excessive amounts of nickel can introduce unduly large amounts of retained austenite during heat treatment and increase the difficulty of annealing the articles of the invention to the low hardnesses needed for some machining operations. The nickel contents of the articles of the invention are therefore best kept to residual amounts or to an amount below about 0.20% when low annealed hardnesses are necessary or when the articles can be rapidly cooled from the austenitizing temperature such as by oil quenching during heat treatment. However, for applications where low annealed hardnesses are not essential or where greater hardenability is desired such as for articles having large cross sections or when the articles cannot be rapidly cooled from the austenitizing temperature, such as in some vacuum hardening operations, it is advantageous to increase their nickel content from 0.20 to 2.00% and preferably from 0.20 to 0.90%, or 0.20 to 0.60%.

Chromium is very important for increasing the corrosion resistance, hardenability, and tempering resistance of the articles of the invention. However, it has been found to have a highly detrimental effect on the metal to metal wear resistance of high vanadium corrosion and wear resistant tool steels and for this reason must be limited in the articles of the invention to the minimums necessary for good corrosion resistance.

Molybdenum, like chromium, is very useful for increasing the corrosion resistance, hardenability, and tempering resistance of the articles of the invention However, excessive amounts reduce hot workability. As is well known, tungsten may be substituted for a portion of the molybdenum in a 2:1 ratio in an amount for example up to about 1%.

Sulfur is useful for improving machinability and grindability through the formation of manganese sulfide. However, it can significantly reduce hot workability and corrosion resistance. In applications where corrosion resistance is paramount, it needs to be kept to a maximum of 0.03% or lower.

When desirable, boron in amounts up to about 0.005% can be added to improve the hot workability of the articles of the invention.

The alloys used to produce the nitrogen atomized, high vanadium, prealloyed powders used in making the articles of the invention may be melted by a variety of methods, but most preferably are melted by air, vacuum, or pressurized induction melting techniques. However, the temperatures used in melting and atomizing the alloys, in particular for those containing more than about 12% vanadium, and the temperatures used in hot isostatically compacting the powders must be closely controlled to obtain the fine carbide or carbonitride sizes necessary to achieve good toughness and grindability while maintaining greater amounts of these carbides or carbonitrides to achieve the desired levels of metal to metal and abrasive wear resistance.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is an electron photomicrograph showing the size and distribution of the primary carbides in a high vanadium PM tool steel article of the invention containing 13.57% chromium and 8.90% vanadium (Bar 95-6).

FIG. 2 is an electron photomicrograph showing the size and distribution of the primary carbides in a high vanadium PM tool steel article of the invention containing 13.31% chromium and 14.47% vanadium (Bar 95-23).

FIG. 3 is a graph showing the effect of chromium content on the metal to metal (crossed cylinder) wear resistance of PM tool steels containing about 9.0% vanadium.

FIG. 4 is a graph showing the effect of vanadium content on the metal to metal (crossed cylinder) wear resistance of PM tool steels containing from about 12 to 14% and from about 16 to 24% chromium.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS

TABLE I__________________________________________________________________________Chemical Composition of Experimental Materials AtomizationBar No. Heat No. Temp .degree. F. C Mn P S Si Ni Cr V Mo N O Comments__________________________________________________________________________89-163 515-656 -- 1.78 1.04 -- -- 0.90 -- 12.63 6.33 0.21 0.09 -- 0.20% C added95-21 P69231-2 -- 2.16 0.51 0.016 0.017 0.46 0.11 13.25 8.53 1.04 0.079 0.0166 --95-5 P69230-1 -- 2.14 0.50 0.017 0.016 0.47 0.13 13.30 8.55 1.04 0.08 0.0220 --95-6 L517 2880 2.25 0.49 0.017 0.005 0.58 0.01 13.57 8.90 1.03 0.098 0.0105 --88-107 517-752 -- 2.12 0.45 0.015 0.017 0.71 0.43 12.11 8.96 1.13 0.05 0.0185 --91-17 P77324-2 -- 2.15 0.40 0.024 0.015 0.47 0.52 12.32 8.80 1.02 0.07 0.0180 --90-60 518-011 -- 2.30 0.53 0.017 0.001 0.52 0.88 11.77 9.27 1.05 0.047 0.0050 --95-24 L526 2860 1.91 0.33 0.019 0.004 0.50 -- 13.40 8.94 0.99 0.32 0.0136 --95-240 L526 + C -- 2.01 -- -- -- -- -- -- -- -- -- -- 0.10% C added95-241 L526 + C -- 2.10 -- -- -- -- -- -- -- -- -- -- 0.20% C added95-342 L612 -- 1.95 0.56 -- 0.006 0.58 -- 13.33 8.86 1.06 0.458 -- --95-341 L612 + C -- 2.10 -- -- -- -- -- -- -- -- -- -- 0.15% C added95-7 L520 2860 2.84 0.51 0.017 0.004 0.58 -- 13.43 11.96 1.06 0.104 0.0135 --95-8 L521 2840 2.78 0.47 0.014 0.004 0.62 -- 13.53 11.96 2.72 0.093 0.0137 --95-207 L521 + C -- 2.94 -- -- -- -- -- -- -- -- -- -- 0.20% C added95-23 L525 2860 3.24 0.47 0.020 0.004 0.53 -- 13.31 14.47 1.08 0.12 0.026 --__________________________________________________________________________

To demonstrate the principles of the invention, a series of alloys were produced by induction melting and then nitrogen atomizing. The chemical compositions, in percent by weight, and the atomizing temperatures for these alloys are given in Table I above. Also several commercial ingot cast or powder metallurgy wear or wear and corrosion resistant alloys were obtained and tested for comparison. The chemical compositions of these commercial alloys are given In Table II.

TABLE II__________________________________________________________________________Chemical Composition of Materials Tested for ComparisonMaterial Bar No. Heat C Mn P S Si Ni Cr V Mo W N O Cmmnts__________________________________________________________________________A - Powder Metallurgy MaterialsCPM10 V 85-34 P67018-1 2.51 0.51 0.021 0.085 0.89 0.06 5.25 9.63 1.25 0.01 0.038 0.014 --CPM10 V 93-16 P66210-2 2.45 0.50 0.022 0.073 0.89 -- 5.31 9.74 1.28 -- 0.055 0.017 --K190 90-136 -- 2.28 0.30 0.019 0.018 0.36 0.12 12.50 4.60 1.11 0.17 0.067 -- --Elmax 90-99 -- 1.70 0.30 -- 0.011 0.31 0.19 17.90 3.37 1.09 0.08 0.10 -- --CPM440 V 93-48 P66899-2 2.21 0.39 0.018 0.017 0.42 0.10 16.71 5.26 0.40 -- 0.059 -- --CPM440 V 87-152 P70144-1 2.11 0.41 0.023 0.025 0.43 0.18 16.89 5.34 0.42 -- 0.050 -- --CPM440 V 93-73 P77797-1 2.14 0.40 0.022 0.019 0.38 -- 16.98 5.39 0.40 0.045 0.072 -- --CPM440 91/16 P77326-2 1.89 0.44 0.026 0.015 0.44 0.60 17.32 6.34 1.09 0.03 0.06 -- --VM (6 V)CPM440 91-90 L8 2.54 0.44 0.017 0.006 0.23 0.53 17.75 8.80 1.30 -- 0.16 -- --VM (9 V)M390 90-100 -- 1.89 0.26 -- 0.017 0.21 0.16 19.00 4.23 1.02 0.51 0.11 -- -- 90-137 1.87 0.27 0.019 0.020 0.33 0.14 18.86 4.34 0.97 0.49 0.15 0.0260MPL-1 91-12 P63231 3.74 0.48 0.019 0.012 0.48 0.12 24.21 9.02 3.01 -- 0.079 0.019 --B - Conventional Ingot Cast MaterialsD-7 75-36 -- 2.35 0.34 0.020 0.005 0.32 0.31 12.75 4.43 1.18 0.26 0.037 0.0034 --440B -- -- 0.89 0.37 0.017 0.017 0.35 0.17 18.5 0.10 0.84 0.02 0.04 0.027 --440C -- A18017 1.03 0.47 0.024 0.002 0.44 -- 16.84 -- 0.53 -- 0.04 -- --__________________________________________________________________________

The laboratory alloys in Table I were processed by (1) screening the prealloyed powders to -16 mesh size (U.S. standard), (2) loading the screened powder into five-inch diameter by six-inch high mild steel containers, (3) vacuum outgassing the containers at 500.degree. F., (4) sealing the containers, (5) heating the containers to 2065.degree. F. for four hours in a high pressure autoclave operating at about 15 ksi, and (6) then slowly cooling them to room temperature. In some instances, small amounts of carbon (graphite) were mixed with the powders before loading them into the containers to systematically increase their carbon content. All the compacts were readily hot forged to bars using a reheating temperature of 2050.degree. F. Test specimens were machined from the bars after they had been annealed using a conventional tool steel annealing cycle, which involves heating at 1650.degree. F. for 2 hours, slowly cooling to 1200.degree. F. at a rate not to exceed 25.degree. F. per hour, and then air cooling to ambient temperature.

Several examinations and tests were conducted to demonstrate the advantages of the PM tool steel articles of the invention and the criticality of their compositions and methods of production. Specifically, tests and examinations were made to evaluate their (1) microstructure, (2) hardness in the heat treated condition, (3) hardenability, (4) Charpy C-notch impact strength, (5) performance in a crossed-cylinder wear test as a measure of metal to metal wear resistance, (6) performance in a pin abrasion test as a measure of abrasive wear resistance, and (7) corrosion resistance in modified aqua regia and boiling acetic acid tests as a measure of corrosion resistance in corrosive plastics and other aggressive materials.

Microstructure

The characteristics of the primary chromium-rich M.sub.7 C.sub.3 -type and vanadium-rich MC-type carbides present in the PM articles of the invention are shown in the electron photomicrographs given in FIGS. 1 and 2. The chromium-rich carbides are gray, while the vanadium-rich carbides are colored black in these photomicrographs. Except for the indicated differences in the amounts of these carbides, it is evident that the carbides in heat treated samples from Bar 95-6, which contains 13.57% chromium and 8.90% vanadium, and Bar 92-23, which contains 13.31% chromium and 14.47% vanadium, are well distributed and similar in size and shape. The maximum sizes of the chromium-rich carbides tend to be larger than those of the vanadium-rich carbides, but in general, the sizes of almost all the carbides do not exceed about 6 microns in their longest dimension. The small sizes of the primary carbides are consistent with the teaching of U.S. Pat. No. 5,238,482, which indicates that the sizes of the vanadium-rich MC-type carbides in high vanadium PM cold work tool steels can be controlled by use of higher than normal atomization temperatures and that small carbide sizes are desirable for achieving good toughness and grindability. However, based on the atomization temperatures for the powders from which Bars 95-6 and 95-23 were made (2880 and 2860.degree. F., respectively), it is clear that the composition of these bars, in particular their high chromium content, permits use of atomization temperatures lower than the minimum of 2910.degree. F. required for controlling the size of the MC-type carbides in the lower chromium high vanadium tool steel particles disclosed in this patent. The ability to use lower atomization temperatures facilitates the production and lowers the cost of producing the powders from which the articles of the invention are made.

To further characterize the microstructure of the powder metallurgical articles of the invention, the volume fraction of the primary chromium-rich M.sub.7 C.sub.3 carbides and the vanadium-rich MC carbides present in heat treated samples of four articles within the scope of the invention (Bars 95-6, 95-7, 95-23, and 95-342) were determined by image analysis and compared to those in a high vanadium, high chromium, powder metallurgy wear and corrosion resistant material of current design (Bar 93-48). The results of the measurements, which are given in Table III, show that the volume fraction of the vanadium-rich MC carbides in the articles of the invention increases with vanadium content and that the volume fraction of the MC carbides generally exceeds at least one third of the total volume of primary carbide present in these articles when they are austenitized at 2050.degree. F. and then tempered at 500.degree. F. In contrast, the commercial PM material after the same heat treatment contains a much smaller proportion of vanadium-rich MC carbides. Compare, for example, the difference in the carbide contents of Bar 93-48 with those of Bar 95-6, which is within the scope of the invention and which contains about the same total volume of primary carbide.

TABLE III__________________________________________________________________________Primary Carbide Volume of Experimental and Commercial Materials* Carbide Content-Volume Percent Total Chromium-Rich Vanadium-Rich PrimaryMaterial Bar No. Heat No. C Cr V Mo N M.sub.7 C.sub.3 MC Carbide__________________________________________________________________________CPM420 V (9 V) 95-6 L517 2.25 13.57 8.90 1.03 0.098 13.5 9.4 22.9CPM420 V (12 V) 95-7 L520 2.84 13.43 11.96 1.02 0.104 15.7 12.6 28.3CPM420 V (14.5 V) 95-23 L525 3.24 13.31 14.47 1.06 0.12 14.6 17.1 31.7CPM420 VN (9 V) 95-342 L612 1.95 13.33 8.86 1.06 0.458 14.9 10.0 24.9CPM440 V 93-48 P66899-2 2.21 16.71 5.26 0.40 0.059 21.5 2.1 23.6__________________________________________________________________________ *Heat Treatment 2050.degree. F./30 minutes, OQ, 500.degree. F./2 + 2 hours. Hardness

Hardness is an important factor affecting the strength, toughness, and wear resistance of martensitic tool steels. In general, a minimum hardness of about 58 HRC is needed with cold work tool steels for them to adequately resist deformation in service. Higher hardnesses are useful for increasing wear resistance, but for corrosion resistant cold work tool steels, the compositions and heat treatments needed to achieve these higher hardnesses often result in a loss of toughness or corrosion resistance. In this regard, Table IV contains data on the carbon and nitrogen levels needed in the PM articles of the invention to achieve a minimum hardness of about 58 HRC when they are austenitized between 2050 and 2150.degree. F., oil quenched, and then tempered in the temperature range (500 to 600.degree. F.) producing best corrosion resistance. They indicate that to achieve the desired hardness response, the carbon and nitrogen levels of these articles must be equal to or exceed the minimums indicated by the following relationship:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V) The importance of this relationship is shown by the hardness data for Bars 95-8 and 95-24, whose combined carbon and nitrogen levels are below the calculated minimums and which as a consequence do not provide the required hardness after the indicated heat treatments. To achieve a hardness of at least 58 HRC with these two materials, it was necessary to increase their carbon contents. With Bar 95-8, which contains 0.093% nitrogen and which has a calculated minimum carbon content of 2.86%, increasing carbon from 2.74% to 2.94%, as with bar 95-207, provided the desired hardness. With Bar 95-24, which contains 0.32% nitrogen and which has a calculated minimum carbon content of 2.01%, increasing carbon from 1.91% to 2.01% as with Bar 95-240, and from 1.91% to 2.10% as with Bar 93-241, produced the desired hardness. Hardenability

Hardenability is an important tool steel property that relates to the depth to which a steel can be fully hardened under a specific set of heating and cooling conditions. For a given section size of an article, it directly affects the rate of cooling needed to fully harden the article over its entire cross section; or conversely, it affects the maximum size of an article that can be fully hardened across its cross section for a given rate of cooling. To demonstrate the strong effect of nickel on the hardenability of the powder metallurgical articles of the invention, small samples of these materials, about 3/4-inch by 3/4-inch by 3/4-inch in size, were austenitized and slowly cooled to room temperature to approximate the cooling rates encountered in the centers of slowly cooled or slack-quenched bars. This was done by heating the samples at 2100.degree. F. for 10 minutes and then by very slowly cooling them to room temperature by rapidly placing them on a heavy section of thermal insulation and then covering them with a layer of the thermal insulation material. After the samples reached room temperature, they were tempered at 500.degree. F. for 2+2 hours and tested for hardness.

Table V contains the results of the slow cooling (hardenability) experiments as well as the annealed and the heat treated hardnesses obtained for four different PM articles (Bars 95-6, 88-107, 91-17, and 90-60) produced with nickel contents of about 0.01, 0.43, 0.52, and 0.88%. In the hardened and tempered condition, the hardnesses of the four steels are almost the same, indicating that for rapidly cooled (oil quenched) samples where hardenability is normally not a consideration, nickel has essentially no effect on their attainable hardness. However, for the slowly cooled samples where hardenability is an important consideration, it can be seen that adding 0.43 to 0.88% nickel significantly increased their hardness from 27 to 54 HRC, indicating that these amounts of nickel have a highly positive effect on their hardenability. A similar effect can be seen for nickel by comparing the annealed hardnesses of the four steels where increasing their nickel contents from about 0.01 to 0.88% significantly increased their annealed hardness from 22 to 31 HRC. These data confirm that when low annealed hardnesses are not essential, nickel can be beneficially used to increase the hardenability of the articles of the invention.

TABLE IV__________________________________________________________________________Heat Treatment Response of Experimental Metals__________________________________________________________________________ Hardness 2050.degree. F./30 minutes, OQ 500.degree. F. 600.degree. F. 750.degree. F.Material Bar No. C Cr V Mo N As Q 2 + 2 hr. 2 + 2 hr. 2 + 2 hr.__________________________________________________________________________CPM 420 V (9 V) 95-6 2.25 13.57 8.90 1.03 0.098 63 59.5 60 60.5CPM 420 V 95-7 2.84 13.43 11.96 1.06 0.104 63.5 60 60.5 61(12 V)CPM 420 V 95-8 2.78 13.53 11.96 2.72 0.093 -- 51 53 53(12 V + Mo)-- 95-207 2.94 -- -- -- -- 63.5 60 60 61CPM 420 V 95-23 3.24 13.31 14.47 1.08 0.12 64 60 61.5 62(14.5 V)CPM 420 VN 95-24 1.91 13.40 8.94 0.099 0.32 60 56 57 57.5-- 95-240 2.01 -- -- -- -- 62 58 58 59.5-- 95-241 2.10 -- -- -- -- 62.5 59 59.5 60CPM 420 VN 95-342 1.95 13.33 8.86 1.06 0.458 62 58 58 59-- 95-341 2.10 -- -- -- -- 63 59 59.5 60__________________________________________________________________________ Hardness Calculated 2150.degree. F./10 minutes, OQ Minimum 500.degree. F. 600.degree. F. 750.degree. F. Carbon Material Bar No. As Q 2 + 2 hr. 2 + 2 hr. 2 + 2 hr. Content*__________________________________________________________________________ CPM 420 V (9 V) 95-6 63 59 59.5 60.5 2.21 CPM 420 V 95-7 63.5 60.5 60.5 61 2.74 (12 V) CPM 420 V 95-8 62.5 59 59 59.5 2.86 (12 V + Mo) -- 95-207 63.5 60 60 61 -- CPM 420 V 95-23 64 61 61 62 3.16 (14.5 V) CPM 420 VN 95-24 61.5 57.5 57.5 58.5 2.01 -- 95-240 61.5 58 58 58.5 -- -- 95-241 62 58.5 58 59.5 -- CPM 420 VN 95-342 61.5 58 58 59 1.87 -- 95-341 62 58 58 59 --__________________________________________________________________________ *(% C + 6/7% N).sub.minimum = 0.40 + 0.099 (% Cr - 11.0) + 0.063 (% Mo) + 0.177 (% V) TABLE V__________________________________________________________________________Effect of Nickel Content on the Hardness of Annealed and of Slow CooledCPM 420 VChemical Composition (Wt. %) Annealed* Slow Cooled** Heat Treated***Bar No. C Ni Cr V Mo N Hardness (HRC) Hardness (HRC) Hardness (HRC)__________________________________________________________________________95-6 2.25 <0.01 13.57 8.90 1.01 0.098 22 27 59 88-107 2.12 0.43 12.11 8.96 1.13 0.05 27.5 53.5 57.591-17 2.15 0.52 12.32 8.80 1.02 0.07 28 54 5890-60 2.30 0.88 11.77 9.27 1.05 0.047 31 54 59__________________________________________________________________________ *Specimens heated at 1650.degree. F. for 2 hours, slow cooled to 1200.degree. F. at a rate not exceeding 25.degree. F. per hour, and then air cooled to room temperature. **Specimens heated at 2100.degree. F. for 10 minutes, slow cooled to room temperature under a thermal blanket and tempered at 500.degree. F. for 2 2 hours. ***Specimens heated at 2050.degree. F. for 30 minutes, oil quenched and tempered at 500.degree. F. for 2 + 2 hours. Impact Toughness

To evaluate the impact toughness of the PM articles of the invention, Charpy C-notch impact tests were conducted at room temperature on heat treated specimens having a notch radius of 0.5 inch. The procedure for the tests was similar to that given in ASTM Standard E23-88. Results obtained for specimens prepared from three different PM articles made within the scope of the invention and for several commercial wear or wear and corrosion resistant alloys are given in Table VI. The results show that the impact toughness of the PM articles of the invention generally decreases with increased vanadium content. They also show that the toughness of the PM articles of the invention, depending on vanadium content, is comparable to or better than that of several widely used conventional ingot cast or PM cold work tool steels, which as shown in Table VII, have much poorer metal to metal wear resistance.

TABLE VI__________________________________________________________________________Charpy C-Notch Impact Properties of Experimental and Commercial ToolSteels Charpy C-Notch Chromium Vanadium Heat Hardness Impact StrengthMaterial Bar No. Heat No. Content Content Treatment** (HRC) (ft - lb)__________________________________________________________________________D-2* -- -- -- -- E 61 17D-4* -- -- -- -- F 61 10D-7* 75-36 -- 12.75 4.43 G 61 7T440C* -- A18017 16.84 -- G 58 16CPM 10 V 93-16 P66210-2 -- -- C 61 18K190 90-136 -- 12.50 4.60 A 59 22CPM 420 V 95-21 P69231-2 13.25 8.53 A 58 23CPM 420 V 95-7 L520 13.43 11.96 A 59 17CPM 420 V 95-23 L525 13.31 14.47 A 58 11.5CPM 440 V 87-152 P70144-1 16.89 5.34 A 58 16MPL-1 91-12 P63231 24.21 9.02 A 63 6.5__________________________________________________________________________ *Conventional ingot cast material. **Heat treatments were as follows: A 2050.degree. F./30 minutes, OQ, 500.degree. F./2 + 2 hours B 2150.degree. F./10 minutes, OQ, 500.degree. F./2 + 2 hours C 2050.degree. F./30 minutes, OQ, 1025.degree. F./2 + 2 hours D 2150.degree. F./10 minutes, OQ, 1000.degree. F./2 + 2 + 2 hours E 1850.degree. F./1 hour, AC, 400.degree. F./2 + 2 hours F 1850.degree. F./1 hour, OQ, 500.degree. F./2 + 2 hours G 1900.degree. F./1 hour, OQ, 400.degree. F./2 + 2 hours H 2100.degree. F./10 minutes, OQ, 500.degree. F./2 + 2 hours I 1975.degree. F./30 minutes, OQ, 500.degree. F./2 + 2 hours Metal to Metal Wear Resistance

The metal to metal wear resistance of the PM articles of the invention and of the materials tested for comparison was measured using an unlubricated crossed-cylinder wear test similar to that described in ASTM Standard G83. In this test, a cylinder of the tool steel to be tested and a cylinder made of cemented tungsten carbide containing 6% cobalt are positioned perpendicular to each other. A 15-pound load is applied to the specimens through a weight on a lever arm. During the test, the tungsten carbide cylinder is rotated at a speed of 667 revolutions per minute. As the test progresses, a wear spot forms on the specimen of the tool steel. At the end of the test, which is conducted for a fixed period of time, the extent of wear is determined by measuring the depth of the wear spot on the specimen and converting it into wear volume by aid of a relationship derived for this purpose. The metal to metal wear resistance, or the reciprocal of the wear rate, is then computed by the following formula: ##EQU1## where: v=the wear volume (in.sup.3)

L=the applied load (lb) s=the sliding distance (in) d=the diameter of the tungsten carbide cylinder (in) and N=the number of revolutions made by the tungsten carbide cylinder (ppm)

The results of the metal to metal (crossed cylinder) wear tests are given in Table VII. They show that the metal to metal wear resistance of PM and conventional wear resistant materials is significantly affected by their chromium and vanadium contents. The highly negative effect of chromium on the resistance to metal to metal wear is illustrated in FIG. 3 which compares the metal to metal wear resistance of CPM 10V (Bar 85-34), CPM 420V (Bar 95-21), CPM 440VM (Bar 91-90), and MPL-1 (Bar 91-12). These materials contain roughly the same amount of vanadium but contain widely different amounts of chromium. In contrast to previous information indicating that higher carbon and chromium contents necessarily improve wear resistance, the figure shows that increasing the chromium content of PM high vanadium, wear and corrosion-resistant tool steels substantially decreases their metal to metal wear resistance. Thus, to increase metal to metal wear resistance, the chromium content of the corrosion resistant, high vanadium martensitic PM tool steels must be limited to the minimums necessary for good corrosion resistance. For this reason, the chromium contents of the PM articles of the invention are restricted to amounts between 11.5 and 14.5%, and preferably between 12.5 and 14.5%.

FIG. 4 shows the effect of vanadium content on the metal to metal wear resistance of two groups of PM wear or wear and corrosion resistant alloys included in Table VII. One group contains from about 12 to 14% chromium and the other from about 16 to 24% chromium. For the group of PM materials containing from about 16 to 24% chromium, it is clear that increasing vanadium content from about 3 to 9% has only a small effect on metal to metal wear resistance. On the other hand, for the group of PM materials containing from about 12 to 14% chromium, increasing vanadium content above about 4%, and particularly about 8%, increases metal to metal wear resistance significantly. For a given vanadium level, it is again evident that chromium has a negative effect and that metal to metal wear resistance is higher for the group of alloys with chromium contents in the range of 12 to 14% than for the group with chromium contents in the range of 16 to 24%. For these reasons, the chromium contents of the PM articles of the invention are restricted to a range between 11.5 and 14.5% and the vanadium contents to a broad range between about 8 to about 15% and preferably within a range of about 12 to 15%.

Abrasive Wear Resistance

The abrasive wear resistance of the experimental materials was evaluated using a pin abrasion test. In this test, a small cylindrical specimen (0.25-inch diameter) is pressed against a dry, 150-mesh garnet abrasive cloth under a load of 15 pounds. The cloth is attached to a movable table which causes the specimen to move about 500 inches in a non-overlapping path over fresh abrasive. As the specimen moves over the abrasive, it is rotated around its own axis. The weight loss of the specimens was used as a measure of material performance.

The results of the pin abrasion tests are given in Table VII. For the PM articles of the invention, it is clear that their abrasive wear resistance generally improves with vanadium content, as can be seen by comparing the weight losses for Bar 95-6 which contains 8.90% vanadium (52 to 53.7 grams) with those for Bar 95-7, which contains 11.96% vanadium (44 to 51.5 grams), and Bar 95-23 which contains 14.47% vanadium (39.5 to 47 grams). Further, it is clear that the abrasive wear resistance of the PM articles of the invention is superior to that of several commercial PM corrosion and wear resistant materials, as can be seen by comparing the weight losses for Bar 95-6 (52 to 53.7 grams) with those of Elmax (70 grams), CPM 440VM (64 grams), and M390 (60 grams).

TABLE VII__________________________________________________________________________Wear Resistance of Experimental and Commercial Tool Steels Cross Pin Cylinder Abrasion Wear Test Heat Hardness Resistance Wt. LossMaterial Bar No. Heat No. C Cr V Mo N Treat.* (HRC) (psi .times. 10.sup.10) (mg) Cmmnts__________________________________________________________________________A. Experimental MaterialsCPM420 89-163 515-656 1.78 12.63 6.33 0.21 0.99 A 58 9 -- 0.20% C added(6 V) B -- -- --CPM420 V 95-6 L517 2.25 13.57 8.90 1.01 0.098 A 59.5 -- 53.7 --(9 V) B 59 12.6 52CPM420 95-21 P69231 2.16 13.25 8.53 1.04 0.079 A 58 13.5 57.9 --(9 V) B 58.5 16.9 50.5CPM420 V 95.7 L520 2.84 13.43 11.96 1.02 0.104 A 60 27.6 51.5 --(12 V) B 60.5 33.1 44CPM420 V 95-8 L521 2.78 13.53 11.96 2.72 0.093 A 51 4.2 65 --(12V - B 59 10.8 49Mo)-- 95-207 L521 + C 2.94 -- -- -- -- A 60 -- 43.3 0.20% C added B 60 53.4 39.1CPM420 V 95-23 L525 3.24 13.31 14.47 1.05 0.12 A 60 45.6 47 --(14.5 V) B 60 59.4 39.5CPM 95-24 L526 1.91 13.40 8.94 0.99 0.32 A 56 6.0 62 --420 VN B 57.5 19.2 50.4-- 95-240 L526 + C 2.01 -- -- -- -- A 58 41 56.5 0.10% C added B 58 48.6 48.7-- 95-241 L526 + C 2.10 -- -- -- -- A 59 38.9 54.5 0.20% C added B 58.5 -- 48.0CPM 95-342 L612 1.95 13.30 8.86 1.06 0.46 A 58 -- 60.5420 VN B 58 53.9-- 95-341 L612 + C 2.10 -- -- -- -- A 59.5 -- 59.2 0.15% C added B 58 53.0B. PM Materials Tested for ComparisonCPM10 V 85-34 P67018 2.51 5.25 9.63 1.25 0.038 C 61 60 45 -- 93.16 P66210-2 2.45 5.31 9.74 1.23 0.055 D 64 65 32K190 90-136 -- 2.28 12.50 4.60 1.11 0.067 A 59 8 46 --Elmax 90-99 -- 1.70 17.90 3.37 1.09 0.10 I 57 2.5 70 --CPM440 V 87-152 -- 2.11 16.89 5.34 0.42 0.05 A 58 4 -- --CPM440 91-16 P77326-2 1.89 17.32 6.34 1.09 0.06 A 57 4 64 --VM (9 V)CPM440 91-90 L8 2.54 17.75 8.80 1.30 0.16 A 58.5 6.5 -- --VM (9 V)M390 90-100 -- 1.89 19.00 4.23 1.02 0.11 H 58 5.1 60 --MPL-1 91-12 P63231 3.74 24.21 9.02 3.01 0.079 A 63 5.5 30.7 -- B 64C. Conventional Ingot Cast MaterialsD2 75-57 -- -- -- -- -- -- E 60 1.7 48.6 --D-7 75-36 -- 2.35 12.75 4.43 1.18 0.037 G 61 -- 30.6 --T440B -- -- 0.89 18.5 0.10 0.84 0.04 I 54 -- 78 --T440C -- A18017 1.03 16.84 -- 0.53 0.04 G 58 3 -- --__________________________________________________________________________ *Heat treatments were as follows: A 2050.degree. F./30 minutes, OQ, 500.degree. F./2 + 2 hours B 2150.degree. F./10 minutes, OQ, 500.degree. F./2 + 2 hours C 2050.degree. F./30 minutes, OQ, 1025.degree. F./2 + 2 hours D 2150.degree. F./10 minutes, OQ, 1000.degree. F./2 + 2 + 2 hours E 1850.degree. F./1 hour, AC, 400.degree. F./2 + 2 hours F 1850.degree. F./1 hour, OQ, 500.degree. F./2 + 2 hours G 1900.degree. F./1 hour, OQ, 400.degree. F./2 + 2 hours H 2100.degree. F./10 minutes, OQ, 500.degree. F./2 + 2 hours I 1975.degree. F./30 minutes, OQ, 500.degree. F./2 + 2 hours Corrosion Resistance

The corrosion resistance of the PM articles of the invention and of several commercial alloys that were included for comparison was evaluated in two different corrosion tests. In one test, samples were immersed for 3 hours at room temperature in an aqueous solution containing 5% nitric acid and 1% hydrochloric acid by volume. The weight losses of the samples were determined and then corrosion rates calculated using material density and specimen surface area. In the other corrosion test, samples were immersed in boiling aqueous solutions of 10% glacial acetic acid by volume for 24 hours. Each sample was immersed in the test solution. The weight loss of each sample was determined, and by using the material density and surface area, the corrosion rate was calculated and used as a measure of material performance.

TABLE VIII__________________________________________________________________________Corrosion Resistance of Experimental and Commercial Tool Steels Dilute Calculated Aqua-Regia Boiling Carbon Heat Hardness 75 F.-3 hr. 10% Acetic Acid Content*Material Bar No. Heat No. C Cr V Mo N Treatment HRC (mils/month) (mils/month) Min. Max. Comments__________________________________________________________________________CPM 95-6 L517 2.25 13.57 8.90 1.01 0.098 A 59 461 153 2.21 2.41420 V B 59.5 536 83CPM 95-7 L520 2.84 13.43 11.96 1.02 0.104 A 60 292 114 2.74 2.94420 V B 60 323 58CPM 95-8 L521 2.78 13.53 11.96 2.72 0.093 A 47.5 110 41 2.86 3.06 Low420 V B 54 45 9 CarbonCPM 95-207 L521 + C 2.94 A 59 322 59 0.20% C420 V B 61 376 80 addedCPM 95-23 L525 3.24 13.31 14.47 1.05 0.12 A 60 219 42 3.16 3.36420 V B 60 218 19CPM 95-24 L526 1.91 13.40 8.94 1.01 0.32 A 55 32 0 2.01 2.21 Low420 VN B 57.5 19 0 Carbon 95-240 L526 + C 2.01 A 58 308 27 -- -- 0.10% C B 59 252 18 added 95-241 L526 + C 2.10 A 59 483 109 -- -- 0.20% C B 58.5 522 48 addedCPM 95-342 L512 1.95 13.33 8.86 1.06 0.46 A 58 585 77 1.87 2.07420 VN B 58 446 42CPM 95-341 L612 + C 2.10 A 59.5 768 311 -- -- 0.15% C420 VN B 58 798 137 added High CarbonB. Commercial PM Materials Tested for ComparisonCPM10 VK190 90-136 2.28 12.50 4.60 1.11 0.067 A 59 1046 640Elmax 90-99 1.70 17.90 3.37 1.09 0.10 I 57.5 692 290CPM 93-73 P77797-1 2.14 16.98 5.39 0.40 0.072 A 1243 429440 V B 915 341CPM 93-48 P66899-2 1.89 17.32 6.34 1.09 0.06 A 1122 462440 V B 1165 485CPM 91-16 P77326-2 1.89 17.32 6.34 1.09 0.06 A 56 362 17440 VM B 57 242 11M390 90-137 1.87 18.86 4.34 0.97 0.15 C 59 563 30MPL-1 91-12 P63231 3.74 24.21 9.02 3.61 -- B 63 445 95C. Conventional Ingot Cast MaterialsD-7 2.35 12.75 4.43 1.18 0.037 61T440B 0.89 18.5 0.10 0.84 0.04 I 54 518 22T440C A18017 1.03 16.84 0.53 0.04__________________________________________________________________________ *Heat treatments were as follows: A 2050.degree. F./30 minutes, OQ, 500.degree. F./2 + 2 hours B 2150.degree. F./10 minutes, OQ, 500.degree. F./2 + 2 hours C 2050.degree. F./30 minutes, OQ, 1025.degree. F./2 + 2 hours D 2150.degree. F./10 minutes, OQ, 1000.degree. F./2 + 2 + 2 hours E 1850.degree. F./1 hour, AC, 400.degree. F./2 + 2 hours F 1850.degree. F./1 hour, OQ, 500.degree. F./2 + 2 hours G 1900.degree. F./1 hour, OQ, 400.degree. F./2 + 2 hours H 2100.degree. F./10 minutes, OQ, 500.degree. F./2 + 2 hours I 1975.degree. F./30 minutes, OQ, 500.degree. F./2 + 2 hours

The results of the corrosion tests are given in Table VIII. They show that the performance of the PM articles of the invention in the dilute aqua regia test is highly dependent on the balance between carbon and nitrogen and the amounts of chromium, molybdenum, and vanadium that they contain. PM articles represented by Bars 95-24 and 95-8 exhibit excellent corrosion resistance in this test, but as shown earlier in Tables IV and VII, their carbon and nitrogen contents are below those needed to achieve a hardness of at least 58 HRC after the indicated heat treatments and to provide the desired degree of metal to metal wear resistance. Increasing carbon or nitrogen content to meet or exceed the minimum amounts needed to achieve a hardness of at least 58 HRC, as with Bars 95-23, 95-7, and 95-240, slightly reduces corrosion resistance in this test, but the levels of corrosion resistance exhibited by these materials are still very high, as long as their carbon and nitrogen contents do not exceed the maximums calculated according to the following relationship:

(%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177 (%V)

The highly negative effect of exceeding the calculated limits of carbon and nitrogen can be seen by comparing the corrosion rates of Bar 95-342 (446 to 585 mils/month), whose carbon content of 1.95% does not exceed the calculated maximum value of 2.07%, with the corrosion rates of Bar 95-341 (768 to 798 mils/month) whose carbon content of 2.10% exceeds the calculated maximum value of 2.07%. The excellent performance of PM articles within the scope of the invention in relation to that of two commercial PM wear or wear and corrosion resistant alloys can be seen by comparing the corrosion rates of Bar 95-23 (218 to 219 mils/month) and Bar 95-240 (252 to 308 mils/month) with those of Bar 90-136 (1046 mils/month), which is representative of current high chromium and vanadium PM wear resistant alloys, and of Bar 93-73 (916 to 1243 mils/month), which is representative of current high chromium and vanadium PM wear and corrosion resistant alloys.

Similar to the results obtained in the dilute aqua regia tests, the results obtained in the boiling acetic acid tests also show that the corrosion resistance of the PM articles of the invention is highly dependent on their carbon and nitrogen balance. Again, Bar 95-24, which contains less than the minimum calculated carbon content, exhibits excellent corrosion resistance. However, as indicated previously, the hardness of this material is too low to provide the desired degree of metal to metal wear resistance. The corrosion resistance of PM articles within the scope of the invention is also quite good in boiling acetic acid, provided their carbon and nitrogen do not exceed the maximums calculated according to the relationship discussed above. The highly negative effect of exceeding the calculated limit of carbon can be seen by comparing the corrosion rates in acetic acid for Bar 95-342 (42 to 77 mils/month), whose carbon content of 1.95% does not exceed the calculated maximum value of 2.07%, with those for Bar 95-341 (137 to 311 mils/month) whose carbon content of 2.10% exceeds the calculated maximum value of 2.07%. The excellent performance of the PM articles of the invention in the acetic acid tests in relation to that of two PM wear or wear and corrosion resistant alloys typical of current art can be seen by comparing the corrosion rates of Bars 95-23 (19 to 42 mils/month) and 95-240 (18 to 27 mils/month) with those of Bars 90-136 (640 mils/month) and 93-73 (341 to 429 mils/month).

The beneficial effect of substituting nitrogen for part of the carbon on the corrosion resistance of the PM articles of the invention can be seen by comparing the corrosion rates of Bars 95-240, 95-241, and 95-6 in the acetic acid tests. These bars contain roughly the same amounts of chromium, molybdenum, and vanadium, but have significantly different carbon and nitrogen contents. As can be seen in Table VIII, Bar 95-240, which contains 2.01% carbon and 0.32% nitrogen, has the lowest corrosion rates (18-27 mils/month) followed in order by Bar 95-241 (48 to 109 mils/month), which contains 2.10% carbon and 0.32% nitrogen, and by Bar 95-6 (83 to 153 mils/month), which contains 2.25% carbon and 0.098% nitrogen,

In summary, the results of the wear and corrosion tests show that the high vanadium PM articles of the invention exhibit a notably improved combination of metal to metal, abrasive, and corrosive wear resistance that is unmatched by corrosion and wear resistant tool steels of current design. The improved properties of these PM articles are based on the discovery that the metal to metal wear resistance of corrosion resistant, high vanadium PM tool steels is markedly reduced by chromium content and that for best metal to metal wear resistance their chromium contents must be reduced to the minimum levels necessary for good corrosion resistance. Further, to achieve good corrosion resistance at these lower chromium levels, and to obtain the hardness needed for good metal to metal and abrasive wear resistance, it is essential that the carbon and nitrogen contents of the PM articles of the invention be closely balanced with the chromium, molybdenum, and vanadium contents of the articles according to the indicated relationships. Carbon and nitrogen levels below the calculated minimums slightly improve corrosion resistance, but do not provide sufficient hardness and wear resistance. Carbon and nitrogen levels above the calculated maximums increase attainable hardness, but have a highly detrimental effect on corrosion resistance. Further, nitrogen has been found to improve the corrosion resistance of the PM articles of the invention and can be substituted for part of the carbon in these articles when corrosion resistance is of primary importance.

Further, nickel has been found to substantially increase the hardenability of the PM articles of the invention and can be beneficially used in these articles when low annealed hardnesses are not essential.

The properties of the PM articles of the invention make them particularly useful in monolithic tooling or in hot isostatically pressed (HIP) or mechanically clad composites used in the production of reinforced plastics, such as in alloy steel clad barrels, barrel liners, screw elements, check rings, and nonreturn valves. Other potential applications include corrosion resistant bearings, knives, and scrapers used in food processing, and corrosion resistant dies and molds.

The term M.sub.7 C.sub.3 carbide as used herein refers to chromium-rich carbides characterized by hexagonal crystal structure wherein "M" represents the carbide forming element chromium and smaller amounts of other elements such as vanadium, molybdenum, and iron that may also be in the carbide. The term also includes variations thereof known as carbonitrides wherein some of the carbon is replaced by nitrogen.

The term MC carbide as used herein refers to vanadium-rich carbides characterized by a cubic crystal structure wherein "M" represents the carbide forming element vanadium, and small amounts of other elements such as molybdenum, chromium, and iron that may also be present in the carbide. The term also includes the vanadium-rich M.sub.4 C.sub.3 carbide and variations known as carbonitrides wherein some of the carbon is replaced by nitrogen.

All percentages are in weight percent, unless otherwise indicated.

Claims

1. A fully dense, corrosion resistant, high vanadium, powder metallurgy cold work tool steel article with high metal to metal wear resistance made from nitrogen atomized prealloyed powders, consisting essentially of, in weight percent, 1.47 to 3.77 carbon, 0.2 to 2.0 manganese, up to 0.10 phosphorus, up to 0.10 sulfur, up to 2.0 silicon, 0.2 to 2.00 nickel, 11.5 to 14.5 chromium, up to 3.00 molybdenum, 8.0 to 15.0 vanadium, 0.03 to 0.46 nitrogen, and balance iron and incidental impurities; wherein carbon and nitrogen are balanced according to the formulas:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

(%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

said articles when hardened and tempered to a hardness of at least 58 HRC having a volume fraction of primary M.sub.7 C.sub.3 and MC carbides between 16 and 36% in which the volume of MC carbide is at least one third of the total primary carbide volume and where the maximum sizes of the primary carbides do not exceed about six microns in their largest dimension, and wherein, as defined herein, a metal to metal wear resistance of at least 10.times.10.sup.10 psi is achieved.

2. A fully dense, corrosion resistant high vanadium, powder metallurgy cold work tool steel article made from nitrogen atomized prealloyed powders, consisting essentially of, in weight percent, 1.83 to 3.77 carbon, 0.2 to 1.0 manganese, up to 0.05 phosphorus, up to 0.03 sulfur, 0.2 to 1.00 silicon, 0.20 to 2.00 nickel, 12.5 to 14.5 chromium, 0.5 to 3.00 molybdenum, 8.0 to 15.0 vanadium, 0.03 to 0.19 nitrogen, and balance iron with incidental impurities, wherein carbon and nitrogen are balanced according to the formulas:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

(%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

said articles when hardened and tempered to a hardness of at least 58 HRC having a volume fraction of primary M.sub.7 C.sub.3 and MC carbides between 16 and 36% in which the volume of MC carbide is at least one third of the total carbide volume and where the maximum sizes of the primary carbides do not exceed about six microns in their largest dimension and wherein, as defined herein, a metal to metal wear resistance of at least 10.times.10.sup.10 psi is achieved.

3. A fully dense, corrosion resistant high vanadium powder metallurgy cold work tool steel article made from nitrogen atomized prealloyed powders, containing, in weight percent, 1.60 to 3.62 carbon, 0.2 to 1.0 manganese, up to 0.05 phosphorus, up to 0.03 sulfur, 0.2 to 1.00 silicon, 0.20 to 2.00 nickel, 12.5 to 14.5 chromium, 0.5 to 3.00 molybdenum, 8.0 to 15.0 vanadium, 0.20 to 0.46 nitrogen, and balance iron with incidental impurities, wherein carbon and nitrogen are balanced according to the formulas:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

(%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

said articles when hardened and tempered to a hardness of at least 58 HRC having a volume fraction of primary M.sub.7 C.sub.3 and MC carbides between 16 and 36% in which the volume of MC carbide is at least one third of the total carbide volume and where the maximum sizes of the primary carbides do not exceed about six microns in their largest dimension and wherein, as defined herein, a metal to metal wear resistance of at least 10.times.10.sup.10 psi is achieved.

4. The article of claim 2, wherein the vanadium content is within the range of 12.0 to 15.0 weight percent and carbon is within the range of 2.54 to 3.77 weight percent.

5. The article of claim 3, wherein the vanadium content is within the range of 12.0 to 15.0 weight percent and carbon is within the range of 2.31 to 3.62 weight percent.

6. The article of claims 1, 2, 3, 4, or 5, wherein nickel is within the range of 0.20 to 0.90%.

7. The article of claims 1, 2, 3, 4, or 5, wherein nickel is within the range of 0.20 to 0.60%.

8. A method for producing a fully dense, corrosion resistant, powder metallurgy cold work tool steel article with high metal to metal wear resistance, said method consisting of nitrogen atomizing a molten tool steel alloy consisting essentially of, in weight percent, 1.47 to 3.77 carbon, 0.2 to 2.0 manganese, up to 0.10 phosphorus, up to 0.10 sulfur, up to 2.0 silicon, 0.20 to 2.00 nickel, 11.5 to 14.5 chromium, up to 3.00 molybdenum, 8.0 to 15.0 vanadium, 0.03 to 0.46 nitrogen, and balance iron and incidental impurities; wherein carbon and nitrogen are balanced according to the formulas:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

(%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

at a temperature between 2800 and 3000.degree. F. to produce powder, rapidly cooling the powder to ambient temperature, screening the powder to about -16 mesh (U.S. standard), hot isostatically compacting the powder at a temperature of 2000 to 2100.degree. F. at a pressure of 13 to 16 ksi, hot working, annealing, and hardening the resulting article to at least 58 HRC said resulting article having a volume fraction of primary M.sub.7 C.sub.3 and MC carbides between 16 and 36% in which the volume of MC carbides is at least one third of the primary carbide volume and where the maximum sizes of the primary carbides do not exceed about six microns in their largest dimension, and wherein, as defined herein, a metal to metal wear resistance of at least 10.times.10.sup.10 psi is achieved.

9. The method of claim 8, wherein said powder metallurgical tool steel article consists essentially of, in weight percent, 1.47 to 3.77 carbon, 0.2 to 2.0 manganese, up to 0.10 phosphorus, up to 0.10 sulfur, up to 2.0 silicon, 0.20 to 2.00 nickel, 11.5 to 14.5 chromium, up to 3.00 molybdenum, 8.0 to 15.0 vanadium, 0.03 to 0.46 nitrogen, and balance iron and incidental impurities, wherein carbon and nitrogen are balanced according to the formulas:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

(%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V).

10. The method of claim 8, wherein said powder metallurgical tool steel article consists essentially of, in weight percent, 1.83 to 3.77 carbon, 0.2 to 1.0 manganese, up to 0.05 phosphorus, up to 0.03 sulfur, 0.2 to 1.00 silicon, 0.20 to 2.00 nickel, 12.5 to 14.5 chromium, 0.5 to 3.00 molybdenum, 8.0 to 15.0 vanadium, 0.03 to 0.19 nitrogen, and balance iron with incidental impurities, wherein carbon and nitrogen are balanced according to the formulas:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

(%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V).

11. The method of claim 8, wherein said powder metallurgical tool steel article consists essentially of, in weight percent, 1.60 to 3.62 carbon, 0.2 to 1.0 manganese, up to 0.05 phosphorus, up to 0.03 sulfur, 0.2 to 1.0 silicon, 0.20 to 2.00 nickel, 12.5 to 14.5 chromium, 0.5 to 3.00 molybdenum, 8.0 to 15.0 vanadium, 0.20 to 0.46 nitrogen, and balance iron with incidental properties, wherein carbon and nitrogen are balanced according to the formulas:

(%C+6/7%N).sub.minimum =0.40+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V);

(%C+6/7%N).sub.maximum =0.60+0.099(%Cr-11.0)+0.063(%Mo)+0.177(%V).

12.

12. The method of claim 10, wherein the vanadium content of the powder metallurgical article is between 12.0 and 15.0 weight percent and carbon is within the range of 2.54 to 3.77 weight percent.

13. The method of claim 11, wherein the vanadium content of the powder metallurgical article is within the range of 12.0 to 15.0 weight percent and carbon is within the range of 2.31 to 3.62 weight percent.

14. The method of claim 8, wherein said nitrogen atomizing is at a temperature between 2840 and 2880.degree. F. and compacting at a temperature of about 2065.degree. F. at a pressure of 15 ksi.

15. The method of claims 8, 9, 10, 11, 12, 13, or 14, wherein nickel is within the range of 0.20 to 0.90%.

16. The method of claims 8, 9, 10, 11, 12, 13, or 14, wherein nickel is within the range of 0.20 to 0.60%.