CA2815059A1 - Material with high resistance to wear - Google Patents
Material with high resistance to wear Download PDFInfo
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- CA2815059A1 CA2815059A1 CA2815059A CA2815059A CA2815059A1 CA 2815059 A1 CA2815059 A1 CA 2815059A1 CA 2815059 A CA2815059 A CA 2815059A CA 2815059 A CA2815059 A CA 2815059A CA 2815059 A1 CA2815059 A1 CA 2815059A1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/248—Thermal after-treatment
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0824—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid
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- Engineering & Computer Science (AREA)
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- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention relates to a production of ledeburite tool steels by means of a powder metallurgical method, which PM materials have isotropic, mechanical properties, improved wear resistance and high hardness potential.
One method essentially consists in subjecting an HIP ingot and/or a semi-finished product produced from this to a full annealing at a temperature of over 1100 °C, but at least 10 °C
below the fusing temperature of the lowest melting structure phase with a duration of over 12 hrs. and increasing the average carbide phase size of the material by at least 65%, the surface shape of which is rounded and the matrix homogenized, after which a further processing of the same into tools with high wear resistance occurs or into parts to which abrasive stress is applied.
The material according to the invention has isotropic, mechanical properties and has in the thermally tempered state a carbide phase proportion of M6C carbides and MC
carbides of at least 7.0 percent by volume at an average carbide phase size of over 2.8 µm in the matrix, in which matrix a carbon concentration of (0.45 to 0.75) percent by weight is present.
One method essentially consists in subjecting an HIP ingot and/or a semi-finished product produced from this to a full annealing at a temperature of over 1100 °C, but at least 10 °C
below the fusing temperature of the lowest melting structure phase with a duration of over 12 hrs. and increasing the average carbide phase size of the material by at least 65%, the surface shape of which is rounded and the matrix homogenized, after which a further processing of the same into tools with high wear resistance occurs or into parts to which abrasive stress is applied.
The material according to the invention has isotropic, mechanical properties and has in the thermally tempered state a carbide phase proportion of M6C carbides and MC
carbides of at least 7.0 percent by volume at an average carbide phase size of over 2.8 µm in the matrix, in which matrix a carbon concentration of (0.45 to 0.75) percent by weight is present.
Description
Material With High Resistance To Wear The invention relates to a production of ledeburite tool steels by means of a powder metallurgical method, which PM materials have isotropic, mechanical properties, improved wear resistance and high hardness potential.
Highly alloyed tool steels, which due to their composition solidify ledeburitically, often have locally in the casting state coarse carbides and carbide clusters in the structure which align themselves in band form during a heat deformation of the cast ingot and ultimately form 0 carbide bands dependent on the deformation direction or form a deformation structure. This crystalline structure determines anisotropic property features of the material with respect to the particular direction of stress on the part.
In order to achieve isotropic and improved material properties of highly alloyed tool steels, it is known to apply a powder metallurgical production method which ensures a homogenous distribution of small carbides in the matrix.
In a PM method, there occurs a separating of liquid steel by high-speed streams of gas into small droplets which solidify at a high rate and thereby form fine carbide phases in these. By means of a subsequent Hot Isostatic Pressing (HIPing) of the powder in a capsule, an HIP
ingot is produced by sintering which is heat-transformable and advantageously at least has a homogenous distribution of small carbide phases in the material.
Materials produced in this manner are in their mechanical properties to the greatest possible extent isotropic and have good workability but have a reduced hardness potential as a result of the matrix structure. For a person skilled in the art, the term hardness potential refers to the extent of the hardness increase during the annealing of a material that is transformed martensitically from the austenite structure region and has retained austenite.
Furthermore, as was found, PM materials can by comparison be slightly less wear resistant for an identical chemical composition of the alloy, even though equally high carbide phase quantities are present in the matrix during a conventional production.
The invention is now based on the object of disclosing a method of the type named at the outset by means of which an improved wear resistance and an increased hardness potential are imparted to PM materials under retention of the isotropy of the mechanical properties.
Furthermore, the invention is aimed at creating a powder metallurgically produced material from a ledeburite tool steel alloy with high hardness potential and high resistance to abrasive wear.
The object is attained according to the invention with a production according to the PM
method of ledeburite machine steel alloys, in which an HIP ingot and/or a semi-finished product made from this is subjected to a full annealing at a temperature of over 1100 C, but at least 10 C below the fusing temperature of the lowest melting structure phase with a duration of over 12 hrs., and the average carbide phase size of the material is increased by at least 65%, the surface shape of which is rounded and the matrix homogenized, after which a further processing of the same into tools with high wear resistance occurs or into parts to which abrasive stress is applied.
The method according to the invention has the advantages that on the one hand the carbide phases are enlarged at temperatures above 1100 C because of diffusion and on the other hand a homogenization of the matrix occurs, wherein in the non-hardened state of the material the strength properties roughly remain the same and the elongation at fracture and in particular the area reduction at fracture are increased, which results in processing and property advantages.
Highly alloyed tool steels, which due to their composition solidify ledeburitically, often have locally in the casting state coarse carbides and carbide clusters in the structure which align themselves in band form during a heat deformation of the cast ingot and ultimately form 0 carbide bands dependent on the deformation direction or form a deformation structure. This crystalline structure determines anisotropic property features of the material with respect to the particular direction of stress on the part.
In order to achieve isotropic and improved material properties of highly alloyed tool steels, it is known to apply a powder metallurgical production method which ensures a homogenous distribution of small carbides in the matrix.
In a PM method, there occurs a separating of liquid steel by high-speed streams of gas into small droplets which solidify at a high rate and thereby form fine carbide phases in these. By means of a subsequent Hot Isostatic Pressing (HIPing) of the powder in a capsule, an HIP
ingot is produced by sintering which is heat-transformable and advantageously at least has a homogenous distribution of small carbide phases in the material.
Materials produced in this manner are in their mechanical properties to the greatest possible extent isotropic and have good workability but have a reduced hardness potential as a result of the matrix structure. For a person skilled in the art, the term hardness potential refers to the extent of the hardness increase during the annealing of a material that is transformed martensitically from the austenite structure region and has retained austenite.
Furthermore, as was found, PM materials can by comparison be slightly less wear resistant for an identical chemical composition of the alloy, even though equally high carbide phase quantities are present in the matrix during a conventional production.
The invention is now based on the object of disclosing a method of the type named at the outset by means of which an improved wear resistance and an increased hardness potential are imparted to PM materials under retention of the isotropy of the mechanical properties.
Furthermore, the invention is aimed at creating a powder metallurgically produced material from a ledeburite tool steel alloy with high hardness potential and high resistance to abrasive wear.
The object is attained according to the invention with a production according to the PM
method of ledeburite machine steel alloys, in which an HIP ingot and/or a semi-finished product made from this is subjected to a full annealing at a temperature of over 1100 C, but at least 10 C below the fusing temperature of the lowest melting structure phase with a duration of over 12 hrs., and the average carbide phase size of the material is increased by at least 65%, the surface shape of which is rounded and the matrix homogenized, after which a further processing of the same into tools with high wear resistance occurs or into parts to which abrasive stress is applied.
The method according to the invention has the advantages that on the one hand the carbide phases are enlarged at temperatures above 1100 C because of diffusion and on the other hand a homogenization of the matrix occurs, wherein in the non-hardened state of the material the strength properties roughly remain the same and the elongation at fracture and in particular the area reduction at fracture are increased, which results in processing and property advantages.
If parts are worked and/or processed after a full annealing with intervals of time according to the invention, then a susceptibility to cracking also under high material stresses, in particular tensile stress, is significantly reduced.
During a thermal tempering by hardening and annealing of highly alloyed material produced according to the invention, high annealing hardness values are already achieved at low hardening temperatures.
Furthermore, it was surprising to find that, for identical carbide phase quantities but considerably increased carbide phase size, for example of 84%, fully annealed and tempered PM materials show in the standard-compliant abrasion test a substantially improved, possibly by more than 30%, wear resistance when compared with standard samples of the same production without full annealing.
The advantages of the invention can be achieved particularly distinctively if a high speed steel material with a chemical composition in percent by weight of:
Carbon (C) 0.8 to 1.4 Chromium (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron are used as a tool steel alloy, wherein the carbon content of the matrix is set to 0.45 to 0.75 and the average carbide phase diameter in this is set to greater than 2.8 1.1.m.
During a thermal tempering by hardening and annealing of highly alloyed material produced according to the invention, high annealing hardness values are already achieved at low hardening temperatures.
Furthermore, it was surprising to find that, for identical carbide phase quantities but considerably increased carbide phase size, for example of 84%, fully annealed and tempered PM materials show in the standard-compliant abrasion test a substantially improved, possibly by more than 30%, wear resistance when compared with standard samples of the same production without full annealing.
The advantages of the invention can be achieved particularly distinctively if a high speed steel material with a chemical composition in percent by weight of:
Carbon (C) 0.8 to 1.4 Chromium (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron are used as a tool steel alloy, wherein the carbon content of the matrix is set to 0.45 to 0.75 and the average carbide phase diameter in this is set to greater than 2.8 1.1.m.
In the above tool steel alloy, the contents of carbon, of important carbide producers and of the element cobalt, which is particularly conducive to the matrix strength and hot hardness, as well as the carbon concentration of the matrix are specified within limits which, as the materials tests have shown, are essential for the method, wherein an advantageous carbide phase diameter according to the invention is set.
Comparatively coarse carbide phase diameters of this type are also retained in the structural compound under harsh, abrasive stresses, or they are not discharged or dissolved out, because the matrix containing these hard phases had property features advantageous therefor imparted to it by the full annealing.
The method according to the invention can also be applied in an advantageous manner for a cold work steel material with a chemical composition in percent by weight of:
Carbon (C) 1.0 to 3.0 Chromium (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron.
The additional object of the invention is attained by the creation of a material, which material has isotropic, mechanical properties and has in the thermally tempered state a carbide phase proportion of M6C carbides and MC carbides of at least 7.0 percent by volume at an average carbide phase size of over 2.8 gm in the matrix, which matrix has a carbon concentration of (0.45 to 0.75) percent by weight.
Comparatively coarse carbide phase diameters of this type are also retained in the structural compound under harsh, abrasive stresses, or they are not discharged or dissolved out, because the matrix containing these hard phases had property features advantageous therefor imparted to it by the full annealing.
The method according to the invention can also be applied in an advantageous manner for a cold work steel material with a chemical composition in percent by weight of:
Carbon (C) 1.0 to 3.0 Chromium (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron.
The additional object of the invention is attained by the creation of a material, which material has isotropic, mechanical properties and has in the thermally tempered state a carbide phase proportion of M6C carbides and MC carbides of at least 7.0 percent by volume at an average carbide phase size of over 2.8 gm in the matrix, which matrix has a carbon concentration of (0.45 to 0.75) percent by weight.
An carbide phase proportion of equal size has, as was found, a wear-reducing effect if an increased average carbide phase size is present in a homogenous matrix.
According to the prior art, it has up to now been attempted to set carbide phases using the smallest possible size in the material in order to improve or to optimize the property features thereof altogether.
It was surprisingly discovered, however, that increased average carbide phase sizes in the matrix homogenized by means of full annealing cause a substantially improved wear to resistance of the material.
This improvement is not yet fully resolved scientifically; however, it is assumed by the Applicant that under a wear stress the coarser carbides delay a critical decrease in size of the compound surfaces or bonding surfaces in the homogenous matrix, and that the homogenized matrix has larger bonding potentials to the coalesced, coarser carbide.
The improvements in wear resistance are particularly marked for materials which have a chemical composition in percent by weight of:
Carbon (C) 0.8 to 1.4 Chromium (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron, and carbide phases, namely 5.5 to 8.5 percent by volume M6C carbides and 1.5 to 3.9 percent by volume MC carbides, with a rounded surface shape are intercalated in the matrix.
It is thereby advantageous and conducive to the level of the mechanical properties if the material has a percent by weight content of at least one element of:
Si = 0.1 to 0.5, preferably 0.15 to 0.3 max. 0.03, preferably max. 0.02 max. 0.3, preferably max. 0.03 io N = max. 0.1, preferably max. 0.08 If the material has a percent by weight concentration of at least one element of:
= 0.9 to 1.4, preferably 1.0 to 1.3 Mn = 0.15 to 0.5, preferably 0.2 to 0.35 15 Cr = 3.0 to 5.0, preferably 3.5 to 4.5 Mo = 3.0 to 10.0 W = 1.0 to 10.0 Mo+W/2 = 6.5 to 12.0, preferably 7.0 to 11.0 V = 0.9 to 6.0, preferably 1.0 to 4.5 20 Co = 7.0 to 11.0, preferably 8.0 to 10.0 an optimization of the property parameters thereof with respect to necessary specific stresses can occur.
According to the prior art, it has up to now been attempted to set carbide phases using the smallest possible size in the material in order to improve or to optimize the property features thereof altogether.
It was surprisingly discovered, however, that increased average carbide phase sizes in the matrix homogenized by means of full annealing cause a substantially improved wear to resistance of the material.
This improvement is not yet fully resolved scientifically; however, it is assumed by the Applicant that under a wear stress the coarser carbides delay a critical decrease in size of the compound surfaces or bonding surfaces in the homogenous matrix, and that the homogenized matrix has larger bonding potentials to the coalesced, coarser carbide.
The improvements in wear resistance are particularly marked for materials which have a chemical composition in percent by weight of:
Carbon (C) 0.8 to 1.4 Chromium (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron, and carbide phases, namely 5.5 to 8.5 percent by volume M6C carbides and 1.5 to 3.9 percent by volume MC carbides, with a rounded surface shape are intercalated in the matrix.
It is thereby advantageous and conducive to the level of the mechanical properties if the material has a percent by weight content of at least one element of:
Si = 0.1 to 0.5, preferably 0.15 to 0.3 max. 0.03, preferably max. 0.02 max. 0.3, preferably max. 0.03 io N = max. 0.1, preferably max. 0.08 If the material has a percent by weight concentration of at least one element of:
= 0.9 to 1.4, preferably 1.0 to 1.3 Mn = 0.15 to 0.5, preferably 0.2 to 0.35 15 Cr = 3.0 to 5.0, preferably 3.5 to 4.5 Mo = 3.0 to 10.0 W = 1.0 to 10.0 Mo+W/2 = 6.5 to 12.0, preferably 7.0 to 11.0 V = 0.9 to 6.0, preferably 1.0 to 4.5 20 Co = 7.0 to 11.0, preferably 8.0 to 10.0 an optimization of the property parameters thereof with respect to necessary specific stresses can occur.
For cold work steels, which are to withstand the highest stresses in abrupt operation with the aforementioned advantages, it is advantageous if the material has a chemical composition in percent by weight of:
Carbon (C) 0.8 to 3.0 Chromium (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron.
In the following, the invention is described in greater detail on the basis of test results shown merely as an example, along with illustrations of the development work.
The following shows:
Tab. 1 Chemical composition of tested materials Tab. 2 Chemical composition of the matrix of the comparison alloy and of the material according to the invention (S599PM-H) Fig. 1 Mechanical properties of the materials Fig. 2 Carbide phases in the PM material (S599PM) produced according to the prior art (SEM analysis) Fig. 3 Carbide phases in the PM material (S599PM-H) produced according to the invention (SEM analysis) Fig. 4 Carbide phases in the material according to the invention (S599PM-H) (SEM
analysis) Fig. 5 M6C phase from Fig. 4 Fig. 6 MC phase from Fig. 4 Fig. 7 Phase image of a PM material (S599PM) according to the prior art, tempered Fig. 8 Phase image of a PM material (S599PM-H) produced according to the invention, tempered Fig. 9 Phase image of a cast and deformed material (S500) Fig. 10 Device for testing the wear performance (schematic) The SEM analyses (Figs. 3 through 4) occurred using a scanning electron microscope:
SEM model: JEOL JSM 6490 HV
to EDX model: Oxford Instrument sinca-Pentafet x3 Si (Li) 30 mm2 (Fig. 5, 6) The M6C and MC carbide phases were created by means of carbide phase selection using the image processing software: Image J.
From Tab. I, the chemical composition of a standard alloy (AISI type M42) with the designation S500 and that of a powder metallurgically produced material S599PM
as well as that of a material S599PM-H according to the invention can be recognized.
The material with the designation S500 served as a comparison material of typical manufacture, because this has good wear properties according to the prior art.
The alloy corresponding to the composition designated as S599 was smelted, and an HIP
ingot was produced from this according to the PM method, turning the molten mass into powder by nozzle atomization using nitrogen ¨ filling a capsule with this and hot isostatic pressing of the same.
Carbon (C) 0.8 to 3.0 Chromium (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron.
In the following, the invention is described in greater detail on the basis of test results shown merely as an example, along with illustrations of the development work.
The following shows:
Tab. 1 Chemical composition of tested materials Tab. 2 Chemical composition of the matrix of the comparison alloy and of the material according to the invention (S599PM-H) Fig. 1 Mechanical properties of the materials Fig. 2 Carbide phases in the PM material (S599PM) produced according to the prior art (SEM analysis) Fig. 3 Carbide phases in the PM material (S599PM-H) produced according to the invention (SEM analysis) Fig. 4 Carbide phases in the material according to the invention (S599PM-H) (SEM
analysis) Fig. 5 M6C phase from Fig. 4 Fig. 6 MC phase from Fig. 4 Fig. 7 Phase image of a PM material (S599PM) according to the prior art, tempered Fig. 8 Phase image of a PM material (S599PM-H) produced according to the invention, tempered Fig. 9 Phase image of a cast and deformed material (S500) Fig. 10 Device for testing the wear performance (schematic) The SEM analyses (Figs. 3 through 4) occurred using a scanning electron microscope:
SEM model: JEOL JSM 6490 HV
to EDX model: Oxford Instrument sinca-Pentafet x3 Si (Li) 30 mm2 (Fig. 5, 6) The M6C and MC carbide phases were created by means of carbide phase selection using the image processing software: Image J.
From Tab. I, the chemical composition of a standard alloy (AISI type M42) with the designation S500 and that of a powder metallurgically produced material S599PM
as well as that of a material S599PM-H according to the invention can be recognized.
The material with the designation S500 served as a comparison material of typical manufacture, because this has good wear properties according to the prior art.
The alloy corresponding to the composition designated as S599 was smelted, and an HIP
ingot was produced from this according to the PM method, turning the molten mass into powder by nozzle atomization using nitrogen ¨ filling a capsule with this and hot isostatic pressing of the same.
One part of this HIP ingot was processed in a customary manner into samples and tools with the designation S599-PM.
On the second part of the ingot material from the same molten mass, a full annealing according to the invention occurred on the semi-finished product with a square cross section of 100 mm at 1180 C with a duration of 24 hours, and a subsequent further processing of the material with the designation S599PM-H occurred.
to Tab. 2 illustrates the chemical composition of the matrix and the portions of carbide phases in the comparison material S500 and in the material S599PM-H produced according to the invention.
In Fig. 1, the mechanical properties, namely elongation limit11.02, tensile strength Rrn, elongation at fracture A and area reduction at fracture Z, of the materials S500, S599PM and S599PM-H are shown in a bar graph.
As a result of the full annealing according to the invention, the elongation A
and the area reduction Z of the material S599PM-H are clearly increased, which is caused by a homogenization of the matrix.
Fig. 2 shows in micrograph a material S599PM in the soft-annealed state with carbide phases of the type M6C and MC in the matrix. The phase size of the carbides is on average approx.
2.0 um.
The fine M23C6 carbides are not included in the evaluation of the material with a hardness of approx. 258 14B.
On the second part of the ingot material from the same molten mass, a full annealing according to the invention occurred on the semi-finished product with a square cross section of 100 mm at 1180 C with a duration of 24 hours, and a subsequent further processing of the material with the designation S599PM-H occurred.
to Tab. 2 illustrates the chemical composition of the matrix and the portions of carbide phases in the comparison material S500 and in the material S599PM-H produced according to the invention.
In Fig. 1, the mechanical properties, namely elongation limit11.02, tensile strength Rrn, elongation at fracture A and area reduction at fracture Z, of the materials S500, S599PM and S599PM-H are shown in a bar graph.
As a result of the full annealing according to the invention, the elongation A
and the area reduction Z of the material S599PM-H are clearly increased, which is caused by a homogenization of the matrix.
Fig. 2 shows in micrograph a material S599PM in the soft-annealed state with carbide phases of the type M6C and MC in the matrix. The phase size of the carbides is on average approx.
2.0 um.
The fine M23C6 carbides are not included in the evaluation of the material with a hardness of approx. 258 14B.
Fig 3 shows in micrograph the material S599PM-H, which was produced according to the invention. At identical carbide phase proportions, the carbides are significantly coarsened and have an average diameter of approx. 4.0 um.
In the matrix with a hardness of approx. 254 HB, fine M23C6 carbides are again intercalated because the material is present in the soft-annealed state.
Fig. 4 shows a material S599PM-H produced according to the invention in an SEM
analysis (scanning electron microscope), which material is tempered to a hardness of 68.7 HRC.
With respect to Fig. 4 and Fig. 5, it should also be noted that the M23C6 carbides no longer appear in the image after a tempering.
In Fig. 5, the carbide phases of the type M6C, selected using an aforementioned image program, can be seen.
The M6C carbide phase proportion is approx. 7.4 percent by volume, wherein this value resulted from more than 6 measurements as a mean value_ In Fig. 6 the carbide phases of the type MC are illustrated from the testing of the tempered material with a proportion of approx. 1.8 percent by volume, wherein the mean value was likewise calculated from more than 6 measurements.
Fig. 7 shows in a micrograph (polished, solvent-etched using 3% HNO3) a powder metallurgically produced material S599 PM in the thermally tempered state having a homogenous distribution of the fine carbides with a medium carbide phase size of 1.6 um.
The material hardness is approx. 68.2 HRC.
In Fig. 8, the same material, which is tempered using identical parameters, which however was subjected to a full annealing according to the invention, is shown in micrograph, wherein the measurements of the medium carbide phase size yielded a value of 3.6 ttm.
Fig. 9 shows the structure of a material S500 produced using a cast ingot in micrograph in the annealed state with a hardness of 239 FIB, which material has angular, coarser carbide phases arranged slightly bandwise.
Tests concerning the wear performance of the materials occurred by means of a device which is illustrated schematically in Fig. 10.
In the abrasion wear test, samples on a disc which had a diameter of 300 mm and was fitted with SiC abrasive paper P120 were pressed on using a contact force per sample of 13.33 N, which corresponded to a surface pressure of 0.265 Nimm2. The rotation speed of the disc was 150 and 300 The results of the abrasion wear test of tempered samples from respectively 12 tests were valued at 100% for the comparison material S500.
The powder metallurgically produced tempered material S599PM of the same type with fine carbide phases exhibited by comparison a wear rate of approx. 98%.
The tests of the material S599PM-H, which was treated according to the invention using full annealing during production and produced under the same tempering parameters, exhibited an increase in wear resistance of 33% to approx. 130% of the value of S500 and S599PM.
_
In the matrix with a hardness of approx. 254 HB, fine M23C6 carbides are again intercalated because the material is present in the soft-annealed state.
Fig. 4 shows a material S599PM-H produced according to the invention in an SEM
analysis (scanning electron microscope), which material is tempered to a hardness of 68.7 HRC.
With respect to Fig. 4 and Fig. 5, it should also be noted that the M23C6 carbides no longer appear in the image after a tempering.
In Fig. 5, the carbide phases of the type M6C, selected using an aforementioned image program, can be seen.
The M6C carbide phase proportion is approx. 7.4 percent by volume, wherein this value resulted from more than 6 measurements as a mean value_ In Fig. 6 the carbide phases of the type MC are illustrated from the testing of the tempered material with a proportion of approx. 1.8 percent by volume, wherein the mean value was likewise calculated from more than 6 measurements.
Fig. 7 shows in a micrograph (polished, solvent-etched using 3% HNO3) a powder metallurgically produced material S599 PM in the thermally tempered state having a homogenous distribution of the fine carbides with a medium carbide phase size of 1.6 um.
The material hardness is approx. 68.2 HRC.
In Fig. 8, the same material, which is tempered using identical parameters, which however was subjected to a full annealing according to the invention, is shown in micrograph, wherein the measurements of the medium carbide phase size yielded a value of 3.6 ttm.
Fig. 9 shows the structure of a material S500 produced using a cast ingot in micrograph in the annealed state with a hardness of 239 FIB, which material has angular, coarser carbide phases arranged slightly bandwise.
Tests concerning the wear performance of the materials occurred by means of a device which is illustrated schematically in Fig. 10.
In the abrasion wear test, samples on a disc which had a diameter of 300 mm and was fitted with SiC abrasive paper P120 were pressed on using a contact force per sample of 13.33 N, which corresponded to a surface pressure of 0.265 Nimm2. The rotation speed of the disc was 150 and 300 The results of the abrasion wear test of tempered samples from respectively 12 tests were valued at 100% for the comparison material S500.
The powder metallurgically produced tempered material S599PM of the same type with fine carbide phases exhibited by comparison a wear rate of approx. 98%.
The tests of the material S599PM-H, which was treated according to the invention using full annealing during production and produced under the same tempering parameters, exhibited an increase in wear resistance of 33% to approx. 130% of the value of S500 and S599PM.
_
Claims (8)
1. Method for the production of materials with isotropic, mechanical properties and improved wear resistance and high hardness potential, wherein an HIP slug or HIP ingot is produced from a ledeburite tool steel alloy in the PM method by nozzle atomizing the liquid metal into an alloy powder using nitrogen and by means of a Hot Isostatic Pressing of the same, which HIP ingot and/or a semi-finished product produced from this is subjected to a full annealing at a temperature of over 1100 °C, but at least 10 °C below the fusing temperature of the lowest melting structure phase with a duration of over 12 hrs. and the average carbide phase size of the material is increased by at least 65%, the surface shape of which is rounded and the matrix homogenized, after which a further processing of the same into thermally tempered tools with high wear resistance occurs or into parts to which abrasive stress is applied.
2. Method according to claim 1, in which a high speed steel with a chemical composition in percent by weight of:
Carbon (C) 0.8 to 1.4 Chromium (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron are used as a tool steel alloy, wherein the carbon content of the tempered matrix is set to 0.45 to 0.75 and the average carbide phase diameter in this is set to greater than 2.8 µm, preferably to greater than 3.2 µm.
Carbon (C) 0.8 to 1.4 Chromium (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron are used as a tool steel alloy, wherein the carbon content of the tempered matrix is set to 0.45 to 0.75 and the average carbide phase diameter in this is set to greater than 2.8 µm, preferably to greater than 3.2 µm.
3. Method according to claim 1, in which a cold work steel material with a chemical composition in percent by weight of:
Carbon (C) 1.0 to 3.0 Chromium (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron is used as a tool steel alloy.
Carbon (C) 1.0 to 3.0 Chromium (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron is used as a tool steel alloy.
4. Material with high resistance to abrasive wear made from a ledeburite tool steel alloy, produced according to a method as defined by claim 1, which material has isotropic, mechanical properties and has in the thermally tempered state a carbide phase proportion of M6C and MC of at least 7.0 percent by volume at an average carbide phase size of over 2.8 1.tm in the matrix, which matrix has a carbon concentration of (0.45 to 0.75) percent by weight.
C matrix = (0.45 to 0.75) C (percent by weight)
C matrix = (0.45 to 0.75) C (percent by weight)
5. Material according to claim 4, which has a chemical composition in percent by weight of:
Carbon (C) 0.8 to 1.4 Chromium (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and alternatively Ni, AI, Nb, Ti and impurities and balance iron, and carbide phases, namely 5.5 to 8.5 percent by volume M6C carbides and 1.5 to 3.9 percent by volume MC carbides, with a rounded surface shape are intercalated in the matrix.
Carbon (C) 0.8 to 1.4 Chromium (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and alternatively Ni, AI, Nb, Ti and impurities and balance iron, and carbide phases, namely 5.5 to 8.5 percent by volume M6C carbides and 1.5 to 3.9 percent by volume MC carbides, with a rounded surface shape are intercalated in the matrix.
6. Material according to claim 4 or 5 which has a percent by weight content of at least one element of:
Si = 0.1 to 0.5, preferably 0.15 to 0.3 max. 0.03, preferably max. 0.02 max. 0.3, preferably max. 0.03 N = max. 0.1, preferably max. 0.08
Si = 0.1 to 0.5, preferably 0.15 to 0.3 max. 0.03, preferably max. 0.02 max. 0.3, preferably max. 0.03 N = max. 0.1, preferably max. 0.08
7. Material according to claim 4 through 6 which has a percent by weight concentration of at least one element of:
C = 0.9 to 1.4, preferably 1.0 to 1.3 Mn = 0.15 to 0.5, preferably 0.2 to 0.35 Cr = 3.0 to 5.0, preferably 3.5 to 4.5 Mo = 3.0 to 10.0 W = 1.0 to 10.0 Mo+W/2 = 6.5 to 12.0, preferably 7.0 to 11.0 V = 0.9 to 6.0, preferably 1.0 to 4.5 Co = 7.0 to 11.0, preferably 8.0 to 10.0
C = 0.9 to 1.4, preferably 1.0 to 1.3 Mn = 0.15 to 0.5, preferably 0.2 to 0.35 Cr = 3.0 to 5.0, preferably 3.5 to 4.5 Mo = 3.0 to 10.0 W = 1.0 to 10.0 Mo+W/2 = 6.5 to 12.0, preferably 7.0 to 11.0 V = 0.9 to 6.0, preferably 1.0 to 4.5 Co = 7.0 to 11.0, preferably 8.0 to 10.0
8. Material according to claim 4 which has a chemical composition in percent by weight of:
Carbon (C) 0.8 to 3.0 Chromium (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron.
Carbon (C) 0.8 to 3.0 Chromium (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadium (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N and alternatively Ni, Al, Nb, Ti and impurities and balance iron.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA2815059A CA2815059A1 (en) | 2013-05-06 | 2013-05-06 | Material with high resistance to wear |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA2815059A CA2815059A1 (en) | 2013-05-06 | 2013-05-06 | Material with high resistance to wear |
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| Publication Number | Publication Date |
|---|---|
| CA2815059A1 true CA2815059A1 (en) | 2014-11-06 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA2815059A Abandoned CA2815059A1 (en) | 2013-05-06 | 2013-05-06 | Material with high resistance to wear |
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| CA (1) | CA2815059A1 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106273447A (en) * | 2015-06-03 | 2017-01-04 | 深圳维示泰克技术有限公司 | A kind of filling shape printed for 3D generates method |
| CN114561588A (en) * | 2022-01-20 | 2022-05-31 | 长沙市萨普新材料有限公司 | High-boron high-silicon powder high-speed steel and preparation and application of precursor powder thereof |
-
2013
- 2013-05-06 CA CA2815059A patent/CA2815059A1/en not_active Abandoned
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106273447A (en) * | 2015-06-03 | 2017-01-04 | 深圳维示泰克技术有限公司 | A kind of filling shape printed for 3D generates method |
| CN106273447B (en) * | 2015-06-03 | 2018-11-09 | 深圳维示泰克技术有限公司 | A kind of filling shape generation method for 3D printing |
| CN114561588A (en) * | 2022-01-20 | 2022-05-31 | 长沙市萨普新材料有限公司 | High-boron high-silicon powder high-speed steel and preparation and application of precursor powder thereof |
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