CA2700056A1 - Metallurgical powder composition and method of production - Google Patents
Metallurgical powder composition and method of production Download PDFInfo
- Publication number
- CA2700056A1 CA2700056A1 CA2700056A CA2700056A CA2700056A1 CA 2700056 A1 CA2700056 A1 CA 2700056A1 CA 2700056 A CA2700056 A CA 2700056A CA 2700056 A CA2700056 A CA 2700056A CA 2700056 A1 CA2700056 A1 CA 2700056A1
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- Prior art keywords
- iron
- weight
- based powder
- chromium carbides
- powder
- Prior art date
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- Granted
Links
- 239000000843 powder Substances 0.000 title claims abstract description 103
- 239000000203 mixture Substances 0.000 title claims description 18
- 238000000034 method Methods 0.000 title claims description 6
- 238000004519 manufacturing process Methods 0.000 title abstract description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 86
- 229910052742 iron Inorganic materials 0.000 claims abstract description 41
- 239000011159 matrix material Substances 0.000 claims abstract description 19
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 12
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 12
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 11
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 5
- 239000011651 chromium Substances 0.000 claims description 55
- 229910052804 chromium Inorganic materials 0.000 claims description 35
- -1 chromium carbides Chemical class 0.000 claims description 21
- 238000000137 annealing Methods 0.000 claims description 19
- 239000002245 particle Substances 0.000 claims description 16
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 14
- 239000000314 lubricant Substances 0.000 claims description 10
- 238000005245 sintering Methods 0.000 claims description 10
- 238000005056 compaction Methods 0.000 claims description 7
- 229910002804 graphite Inorganic materials 0.000 claims description 4
- 239000010439 graphite Substances 0.000 claims description 4
- 229910052710 silicon Inorganic materials 0.000 claims description 4
- 239000007787 solid Substances 0.000 claims description 4
- 239000003795 chemical substances by application Substances 0.000 claims description 3
- 230000002708 enhancing effect Effects 0.000 claims description 3
- 238000009692 water atomization Methods 0.000 claims description 3
- 230000013011 mating Effects 0.000 claims 1
- 150000001247 metal acetylides Chemical class 0.000 abstract description 36
- 239000000463 material Substances 0.000 description 17
- 229910052799 carbon Inorganic materials 0.000 description 12
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 9
- 238000005275 alloying Methods 0.000 description 8
- 229910052751 metal Inorganic materials 0.000 description 7
- 239000002184 metal Substances 0.000 description 7
- 229910000997 High-speed steel Inorganic materials 0.000 description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 5
- 239000010955 niobium Substances 0.000 description 5
- 229910052760 oxygen Inorganic materials 0.000 description 5
- 239000001301 oxygen Substances 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000010949 copper Substances 0.000 description 3
- 238000003754 machining Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 150000002739 metals Chemical class 0.000 description 3
- 238000010583 slow cooling Methods 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000009977 dual effect Effects 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910003470 tongbaite Inorganic materials 0.000 description 2
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 1
- 229910001634 calcium fluoride Inorganic materials 0.000 description 1
- 229910002090 carbon oxide Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000003623 enhancer Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000008595 infiltration Effects 0.000 description 1
- 238000001764 infiltration Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000003879 lubricant additive Substances 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052961 molybdenite Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- CWQXQMHSOZUFJS-UHFFFAOYSA-N molybdenum disulfide Chemical compound S=[Mo]=S CWQXQMHSOZUFJS-UHFFFAOYSA-N 0.000 description 1
- 229910052982 molybdenum disulfide Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- QIQXTHQIDYTFRH-UHFFFAOYSA-N octadecanoic acid Chemical compound CCCCCCCCCCCCCCCCCC(O)=O QIQXTHQIDYTFRH-UHFFFAOYSA-N 0.000 description 1
- 239000004482 other powder Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 239000012925 reference material Substances 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000000344 soap Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- 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
- C22C33/0207—Using a mixture of prealloyed powders or a master alloy
-
- 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
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L3/00—Lift-valve, i.e. cut-off apparatus with closure members having at least a component of their opening and closing motion perpendicular to the closing faces; Parts or accessories thereof
- F01L3/02—Selecting particular materials for valve-members or valve-seats; Valve-members or valve-seats composed of two or more materials
-
- 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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L2301/00—Using particular materials
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L2301/00—Using particular materials
- F01L2301/02—Using ceramic materials
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L2303/00—Manufacturing of components used in valve arrangements
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L2820/00—Details on specific features characterising valve gear arrangements
- F01L2820/01—Absolute values
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- General Engineering & Computer Science (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
The present invention relates to an annealed pre-alloyed water atomised iron-based powder suitable for the production of pressed and sintered components having high wear resistance. The iron-based powder comprises 10- below 18% by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb and 0.5-2%, preferably 0.7-2% and most preferably 1 -2%
by weight of C. The powder has a matrix comprising less than 10% by weight of Cr, and comprises large M23C6-type carbides in combination with M7C3-type carbides. The invention also relates to a method for production of the iron-based powder as well as a method for producing a pressed and sintered component having high wear resistance and the component having high wear resistance.
by weight of C. The powder has a matrix comprising less than 10% by weight of Cr, and comprises large M23C6-type carbides in combination with M7C3-type carbides. The invention also relates to a method for production of the iron-based powder as well as a method for producing a pressed and sintered component having high wear resistance and the component having high wear resistance.
Description
METALLURGICAL POWDER COMPOSITION AND METHOD OF
PRODUCTION
Field of the Invention The present invention relates to an iron-based powder.
Especially the invention concerns a powder suitable for the production of wear-resistant products such as valve seat inserts (VSI) as well as a component made from the powder.
Background Art Products having high wear-resistance are extensively used and there is a constant need for less expensive products having the same or better performance as/than existing products. Only valve seats inserts are produced in an amount of more than 1 000 000 000 components annually.
The manufacture of products having high wear-resistance may be based on e.g. powders, such as iron or iron-based powders, including carbon in the form of carbides.
Carbides are very hard and have high melting points, characteristics which give them a high wear resistance in many applications.
This wear resistance often makes carbides desirable as components in steels, e.g. high speed steels (HSS), that require a high wear resistance, such as steels for drills, lathes, valve seat inserts and the likes.
A VSI in a combustion engine is a ring that is inserted where the valve comes in contact with the cylinder head during operation. The VSI is used to limit the wear, caused by the valve, on the cylinder head. This is done by using a material in the VSI that can resist wear better than the cylinder head material, without wearing on the valve. The materials used for VSI are cast materials or more commonly pressed and sintered PM materials.
Producing a valve seat insert with powder metallurgy offers a wide flexibility in composition of the VSI and a very cost effective product. The method of fabricating a PM valve seat insert starts with preparation of a mix which includes all ingredients needed in the final component. The powder mix most commonly includes an iron or low alloyed powder serving as matrix in the final component, elemental alloying elements such as C, Cu, Ni, Co etc which should to a lower or higher extent diffuse into the matrix material and enhance strength and hardness. Further hard phase materials containing carbides and similar phases can be added to increase the wear resistance of the alloy. It is also common to have machinability enhancers added to decrease tool wear when machining the finished product, as well as solid lubricants in order to assist the lubrication during service in the engine.
Further, in all press ready mixes evaporative lubricants are added to assist compaction and ejection of the compacted component. A known VSI
material, produced by Powder Metallurgy, is based on high speed steel powder as carbide containing matrix material. All powders used normally have a particle size of less than 180 pm. The average particle size of the mix is usually between 50 to 100 pm to allow the mix to flow and facilitate production. The alloying and lubricant additives are in many cases finer in particle size compared to the matrix powder to improve distribution of alloying elements in the powder mix and finished component.
The powder mix is then fed into a tool cavity with the shape of a VSI
ring. An axial pressure between 400-900 MPa is applied resulting in a near net shape metallic VSI component having a density between 6.4-7.3 g/cm3.
In some instances dual compaction is used to decrease the use of expensive alloying elements. In dual compaction two different powder mixes are used.
One more expensive with excellent wear properties creating the wear surface of VSI facing the valve and one less costly to give the desired height of the component. After the compaction the individual grains are only loosely bonded through cold welding, and a subsequent sintering operation is required to allow the individual particles to diffuse together and to distribute alloying elements. Sintering is usually performed at temperatures between 1120 C and 1150 C but temperatures up to 1300 C can be used, in a reducing atmosphere usually based on Nitrogen and Hydrogen. During sintering or after, copper can be infiltrated in the pores of the component to increase hardness and strength as well as improve heat conductivity and wear properties. In many cases subsequent heat treatments are performed to reach final properties. In order to achive desired geometrical accuracy of the VSI it is machined to desired size. The final machining is in many cases done after VSI is mounted in the cylinder head. The final machining is done in order to give the VSI and inverted valve profile and to have small dimensional variations.
Examples of conventional iron-based powders with high wear resistance are disclosed in e.g. the US patent 6 679 932, relating to a powder mixture including a tool steel powder with finely dispersed carbides, and the US patent 5 856 625 relating to a stainless steel powder.
W, V, Mo, Ti and Nb are strong carbide forming elements which make these elements especially interesting for the production of wear resistant products. Cr is another carbide forming element. Most of these conventional carbide forming metals are, however, expensive and result in an inconveniently high priced product. Thus, there is a need within the powder metallurgical industry for a less expensive iron-based powder, or high speed steel, which is sufficiently wear resistant for applications such as for valve seats or the like.
As chromium is a much cheaper and more readily available carbide forming metal than other such metals used in conventional powders and hard phases with high wear resistance, it would be desirable to be able to use chromium as principal carbide forming metal. In that way the powder, and thus the compacted product, can be more inexpensively produced.
The carbides of regular high speed steels are usually quite small, but in accordance with the present invention it has now unexpectedly been shown that powders having equally advantageous wear resistance, for e.g.
valve seat applications, may be obtained with chromium as the principal carbide forming metal, provided that a sufficient amount of large carbides exists, supported by a minor amount of finer and harder carbides.
Summary of the Invention An objective of the present invention is thus to provide an inexpensive iron-based powder for the manufacture of powder metallurgical products having a high wear resistance.
This objective, as well as other objectives evident from the discussion below, are according to the present invention achieved through an annealed pre-alloyed water atomised iron-based powder, comprising from 10 to below 18 % by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb, 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C, wherein the iron-based powder has a matrix comprising less than 10% by weight of Cr. Further, the iron-based powder comprises large chromium carbides and finer and harder chromium carbides.
As high Cr amounts in the powder promote formation of large type carbides e.g. of the type M23C6 -, then 18% by weight and above of Cr will give a too low content of fine and hard chromium carbides.
In accordance with the present invention this new powder which achieves the above objectives may be obtained through a method of producing an iron-based powder comprising subjecting an iron-based melt including 10- below 18% by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb and 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C to water atomisation in order to obtain iron-based powder particles, and annealing the powder particles at a temperature, and for a period of time, sufficient for obtaining the desired carbides within the particles.
In preferred embodiments, it has been found that temperatures in the range of 900-1100 C and annealing times in the range of 15-72 hours are sufficient for obtaining the desired carbides within the particles.
Brief description of the drawings Fig. 1 shows the microstructure of OB1 based test material.
Fig. 2 shows the microstructure of M3/2 based test material.
Detailed Description of Preferred Embodiments The pre-alloyed powder of the invention contains chromium, 10-below 18% by weight, at least one of molybdenum, tungsten, vanadium and niobium, 0.5-5% by weight of each, and carbon, 0.5-2%, preferably 0.7-2%
and most preferably 1-2% by weight, the balance being iron, optional other alloying elements and inevitable impurities.
The pre-alloyed powder may optionally include other alloying elements, such as silicon, up to 2% by weight. Other alloying elements or additives may also optionally be included.
It should specifically be noted that the very expensive carbide forming metals niobium and titanium are not needed in the powder of the present invention.
The pre-alloyed powder preferably has an average particle size in the range of 40-100 pm, preferably of about 80 pm.
In preferred embodiments the pre-alloyed powder comprises 12-17% by weight of Cr, such as 15-17% by weight of Cr, e.g. 16% by weight of 5 Cr.
In preferred embodiments the pre-alloyed powder comprises 12-below 18% by weight of Cr, 1-3 wt% of Mo, 1-3,5 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
In most preferred embodiments the pre-alloyed powder comprises 14-below 18 weight of Cr, 1-2 wt% of Mo, 1-2 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
In another most preferred embodiment the pre-alloyed powder comprises 12-below 15 weight of Cr, 1-2 wt% of Mo, 2-3 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
In preferred embodiments, the large chromium carbides are of M23C6_type, (M = Cr, Fe, Mo, W,), i.e. besides Cr as the dominating carbide forming element one or more of Fe, Mo and W may be present.
In preferred embodiments, the finer and harder chromium carbides are of M7C3- type (M = Cr, Fe, V), i.e. besides chromium as the dominating carbide forming element one or more of Fe and V may be present. Both types of carbides may also contain other than the above specified carbide forming elements in small amounts. The powder may further comprise other than the above carbide types.
The large carbides of the inventive powder preferably have an average size in the range of 8-45 pm, more preferably in the range of 8-30 pm, a hardness of about 1100-1300 microvickers and preferably make up 10-30%
by volume of the total powder.
The M,C3 _ type smaller carbides of the inventive powder are smaller and harder than the M23C6 _ type large carbides. The smaller carbides of the inventive powder preferably have an average size below 8 pm, a hardness of about 1400-1600 microvickers and preferably make up 3-10% by volume of the total powder.
As the carbides have an irregular shape, "size" defines the longest extension as measured in a microscope.
PRODUCTION
Field of the Invention The present invention relates to an iron-based powder.
Especially the invention concerns a powder suitable for the production of wear-resistant products such as valve seat inserts (VSI) as well as a component made from the powder.
Background Art Products having high wear-resistance are extensively used and there is a constant need for less expensive products having the same or better performance as/than existing products. Only valve seats inserts are produced in an amount of more than 1 000 000 000 components annually.
The manufacture of products having high wear-resistance may be based on e.g. powders, such as iron or iron-based powders, including carbon in the form of carbides.
Carbides are very hard and have high melting points, characteristics which give them a high wear resistance in many applications.
This wear resistance often makes carbides desirable as components in steels, e.g. high speed steels (HSS), that require a high wear resistance, such as steels for drills, lathes, valve seat inserts and the likes.
A VSI in a combustion engine is a ring that is inserted where the valve comes in contact with the cylinder head during operation. The VSI is used to limit the wear, caused by the valve, on the cylinder head. This is done by using a material in the VSI that can resist wear better than the cylinder head material, without wearing on the valve. The materials used for VSI are cast materials or more commonly pressed and sintered PM materials.
Producing a valve seat insert with powder metallurgy offers a wide flexibility in composition of the VSI and a very cost effective product. The method of fabricating a PM valve seat insert starts with preparation of a mix which includes all ingredients needed in the final component. The powder mix most commonly includes an iron or low alloyed powder serving as matrix in the final component, elemental alloying elements such as C, Cu, Ni, Co etc which should to a lower or higher extent diffuse into the matrix material and enhance strength and hardness. Further hard phase materials containing carbides and similar phases can be added to increase the wear resistance of the alloy. It is also common to have machinability enhancers added to decrease tool wear when machining the finished product, as well as solid lubricants in order to assist the lubrication during service in the engine.
Further, in all press ready mixes evaporative lubricants are added to assist compaction and ejection of the compacted component. A known VSI
material, produced by Powder Metallurgy, is based on high speed steel powder as carbide containing matrix material. All powders used normally have a particle size of less than 180 pm. The average particle size of the mix is usually between 50 to 100 pm to allow the mix to flow and facilitate production. The alloying and lubricant additives are in many cases finer in particle size compared to the matrix powder to improve distribution of alloying elements in the powder mix and finished component.
The powder mix is then fed into a tool cavity with the shape of a VSI
ring. An axial pressure between 400-900 MPa is applied resulting in a near net shape metallic VSI component having a density between 6.4-7.3 g/cm3.
In some instances dual compaction is used to decrease the use of expensive alloying elements. In dual compaction two different powder mixes are used.
One more expensive with excellent wear properties creating the wear surface of VSI facing the valve and one less costly to give the desired height of the component. After the compaction the individual grains are only loosely bonded through cold welding, and a subsequent sintering operation is required to allow the individual particles to diffuse together and to distribute alloying elements. Sintering is usually performed at temperatures between 1120 C and 1150 C but temperatures up to 1300 C can be used, in a reducing atmosphere usually based on Nitrogen and Hydrogen. During sintering or after, copper can be infiltrated in the pores of the component to increase hardness and strength as well as improve heat conductivity and wear properties. In many cases subsequent heat treatments are performed to reach final properties. In order to achive desired geometrical accuracy of the VSI it is machined to desired size. The final machining is in many cases done after VSI is mounted in the cylinder head. The final machining is done in order to give the VSI and inverted valve profile and to have small dimensional variations.
Examples of conventional iron-based powders with high wear resistance are disclosed in e.g. the US patent 6 679 932, relating to a powder mixture including a tool steel powder with finely dispersed carbides, and the US patent 5 856 625 relating to a stainless steel powder.
W, V, Mo, Ti and Nb are strong carbide forming elements which make these elements especially interesting for the production of wear resistant products. Cr is another carbide forming element. Most of these conventional carbide forming metals are, however, expensive and result in an inconveniently high priced product. Thus, there is a need within the powder metallurgical industry for a less expensive iron-based powder, or high speed steel, which is sufficiently wear resistant for applications such as for valve seats or the like.
As chromium is a much cheaper and more readily available carbide forming metal than other such metals used in conventional powders and hard phases with high wear resistance, it would be desirable to be able to use chromium as principal carbide forming metal. In that way the powder, and thus the compacted product, can be more inexpensively produced.
The carbides of regular high speed steels are usually quite small, but in accordance with the present invention it has now unexpectedly been shown that powders having equally advantageous wear resistance, for e.g.
valve seat applications, may be obtained with chromium as the principal carbide forming metal, provided that a sufficient amount of large carbides exists, supported by a minor amount of finer and harder carbides.
Summary of the Invention An objective of the present invention is thus to provide an inexpensive iron-based powder for the manufacture of powder metallurgical products having a high wear resistance.
This objective, as well as other objectives evident from the discussion below, are according to the present invention achieved through an annealed pre-alloyed water atomised iron-based powder, comprising from 10 to below 18 % by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb, 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C, wherein the iron-based powder has a matrix comprising less than 10% by weight of Cr. Further, the iron-based powder comprises large chromium carbides and finer and harder chromium carbides.
As high Cr amounts in the powder promote formation of large type carbides e.g. of the type M23C6 -, then 18% by weight and above of Cr will give a too low content of fine and hard chromium carbides.
In accordance with the present invention this new powder which achieves the above objectives may be obtained through a method of producing an iron-based powder comprising subjecting an iron-based melt including 10- below 18% by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb and 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C to water atomisation in order to obtain iron-based powder particles, and annealing the powder particles at a temperature, and for a period of time, sufficient for obtaining the desired carbides within the particles.
In preferred embodiments, it has been found that temperatures in the range of 900-1100 C and annealing times in the range of 15-72 hours are sufficient for obtaining the desired carbides within the particles.
Brief description of the drawings Fig. 1 shows the microstructure of OB1 based test material.
Fig. 2 shows the microstructure of M3/2 based test material.
Detailed Description of Preferred Embodiments The pre-alloyed powder of the invention contains chromium, 10-below 18% by weight, at least one of molybdenum, tungsten, vanadium and niobium, 0.5-5% by weight of each, and carbon, 0.5-2%, preferably 0.7-2%
and most preferably 1-2% by weight, the balance being iron, optional other alloying elements and inevitable impurities.
The pre-alloyed powder may optionally include other alloying elements, such as silicon, up to 2% by weight. Other alloying elements or additives may also optionally be included.
It should specifically be noted that the very expensive carbide forming metals niobium and titanium are not needed in the powder of the present invention.
The pre-alloyed powder preferably has an average particle size in the range of 40-100 pm, preferably of about 80 pm.
In preferred embodiments the pre-alloyed powder comprises 12-17% by weight of Cr, such as 15-17% by weight of Cr, e.g. 16% by weight of 5 Cr.
In preferred embodiments the pre-alloyed powder comprises 12-below 18% by weight of Cr, 1-3 wt% of Mo, 1-3,5 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
In most preferred embodiments the pre-alloyed powder comprises 14-below 18 weight of Cr, 1-2 wt% of Mo, 1-2 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
In another most preferred embodiment the pre-alloyed powder comprises 12-below 15 weight of Cr, 1-2 wt% of Mo, 2-3 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
In preferred embodiments, the large chromium carbides are of M23C6_type, (M = Cr, Fe, Mo, W,), i.e. besides Cr as the dominating carbide forming element one or more of Fe, Mo and W may be present.
In preferred embodiments, the finer and harder chromium carbides are of M7C3- type (M = Cr, Fe, V), i.e. besides chromium as the dominating carbide forming element one or more of Fe and V may be present. Both types of carbides may also contain other than the above specified carbide forming elements in small amounts. The powder may further comprise other than the above carbide types.
The large carbides of the inventive powder preferably have an average size in the range of 8-45 pm, more preferably in the range of 8-30 pm, a hardness of about 1100-1300 microvickers and preferably make up 10-30%
by volume of the total powder.
The M,C3 _ type smaller carbides of the inventive powder are smaller and harder than the M23C6 _ type large carbides. The smaller carbides of the inventive powder preferably have an average size below 8 pm, a hardness of about 1400-1600 microvickers and preferably make up 3-10% by volume of the total powder.
As the carbides have an irregular shape, "size" defines the longest extension as measured in a microscope.
In order to obtain these large carbides, the pre-alloyed powder is subjected to prolonged annealing, preferably under vacuum. The annealing is preferably performed in the range of 900-1100 C, most preferably at about 1000 C, at which temperature chromium of the pre-alloyed powder reacts with carbon to form chromium carbides.
During the annealing, new carbides are formed and grow and existing carbides continue to grow through reaction between chromium and carbon. The annealing is preferably continued for 15-72 hours, more preferably for more than 48 hours, in order to obtain carbides of desired size.
The longer the duration of the annealing, the larger the carbide grains grow.
However, the annealing consumes lots of energy and might be a production flow bottle neck if it continues for a long time. Thus, although an average chromium carbide grain size of the large chromium carbides of about 20-30 pm may be optimal, it might, depending on priority, be more convenient from an economic point of view to terminate the annealing earlier, when the average chromium carbide grain size of the large chromium carbides is about 10 pm.
Very slow cooling, preferably more than 12 hours, from annealing temperature is applied. Slow cooling will allow further growth of carbides, as a larger amount of carbides is thermodynamically stable at lower temperatures. Slow cooling will also assure that the matrix becomes ferritic, which is important for the compressibility of the powder.
Annealing the powder also has other advantages besides the growth of carbides.
During annealing also the matrix grains grow and the inherent stresses of the powder particles, obtained as a result of the water atomisation, are relaxed. These factors make the powder less hard and easier to compact, e.g. gives the powder higher compressibility.
During annealing, the carbon and oxygen contents of the powder may be adjusted. It is usually desirable to keep the oxygen content low.
During annealing carbon is reacted with oxygen to form gaseous carbon oxide, which reduces the oxygen content of the powder. If there is not enough carbon in the pre-alloyed powder itself, for both forming carbides and reducing the oxygen content, additional carbon, in form of graphite powder, may be provided for the annealing.
During the annealing, new carbides are formed and grow and existing carbides continue to grow through reaction between chromium and carbon. The annealing is preferably continued for 15-72 hours, more preferably for more than 48 hours, in order to obtain carbides of desired size.
The longer the duration of the annealing, the larger the carbide grains grow.
However, the annealing consumes lots of energy and might be a production flow bottle neck if it continues for a long time. Thus, although an average chromium carbide grain size of the large chromium carbides of about 20-30 pm may be optimal, it might, depending on priority, be more convenient from an economic point of view to terminate the annealing earlier, when the average chromium carbide grain size of the large chromium carbides is about 10 pm.
Very slow cooling, preferably more than 12 hours, from annealing temperature is applied. Slow cooling will allow further growth of carbides, as a larger amount of carbides is thermodynamically stable at lower temperatures. Slow cooling will also assure that the matrix becomes ferritic, which is important for the compressibility of the powder.
Annealing the powder also has other advantages besides the growth of carbides.
During annealing also the matrix grains grow and the inherent stresses of the powder particles, obtained as a result of the water atomisation, are relaxed. These factors make the powder less hard and easier to compact, e.g. gives the powder higher compressibility.
During annealing, the carbon and oxygen contents of the powder may be adjusted. It is usually desirable to keep the oxygen content low.
During annealing carbon is reacted with oxygen to form gaseous carbon oxide, which reduces the oxygen content of the powder. If there is not enough carbon in the pre-alloyed powder itself, for both forming carbides and reducing the oxygen content, additional carbon, in form of graphite powder, may be provided for the annealing.
As much of the chromium of the pre-alloyed powder migrates from the matrix to the carbides during annealing, the matrix of the resulting annealed powder has a content of dissolved chromium of less than 10% by weight of the matrix, preferably less than 9% by weight and most preferably less than 8% by weight, why the powder is not stainless.
The matrix composition of the powder is designed such that ferrite transforms to austenite during sintering. Thereby, the austenite can transform into martensite upon cooling after sintering. Large carbides in combination with smaller and harder carbides in a martensitic matrix will give good wear resistance of the pressed and sintered component.
The annealed powder of the invention may be mixed with other powder components, such as other iron-based powders, graphite, evaporative lubricants, solid lubricants, machinability enhancing agents etc, before compaction and sintering to produce a product with high wear resistance. One may e.g. mix the inventive powder with pure iron powder and graphite powder, or with a stainless steel powder. A lubricant, such as a wax, stearate, metal soap or the like, which facilitates the compaction and then evaporates during sintering, may be added, as well as a solid lubricant, such as MnS, CaF2, MoS2, which reduces friction during use of the sintered product and which also may enhance the machinability of the same. Also other machinability enhancing agents may be added, as well as other conventional additives of the powder metallurgical field.
Due to its good compressibility the obtained mix is well suited for compacting into near net shape VSI components having a chamfered inverted valve profile.
Example 1 A melt of 16.0 wt% Cr, 1.5 wt% Mo, 1.5 wt% W, 1 wt% V, 0.5 wt% Si, 1.5 wt% C and balance Fe was water atomised to form a pre-alloyed powder. The obtained powder was subsequently vacuum annealed at 1000 C for about 48 hours, the total annealing time being about 60 hours, after which the powder particles contained about 20% by volume of M23C6-type carbides of an average grain size of about 10 pm and about 5% by volume of M,C3-type carbides of an average grain size of about 3 pm in a ferritic matrix.
The matrix composition of the powder is designed such that ferrite transforms to austenite during sintering. Thereby, the austenite can transform into martensite upon cooling after sintering. Large carbides in combination with smaller and harder carbides in a martensitic matrix will give good wear resistance of the pressed and sintered component.
The annealed powder of the invention may be mixed with other powder components, such as other iron-based powders, graphite, evaporative lubricants, solid lubricants, machinability enhancing agents etc, before compaction and sintering to produce a product with high wear resistance. One may e.g. mix the inventive powder with pure iron powder and graphite powder, or with a stainless steel powder. A lubricant, such as a wax, stearate, metal soap or the like, which facilitates the compaction and then evaporates during sintering, may be added, as well as a solid lubricant, such as MnS, CaF2, MoS2, which reduces friction during use of the sintered product and which also may enhance the machinability of the same. Also other machinability enhancing agents may be added, as well as other conventional additives of the powder metallurgical field.
Due to its good compressibility the obtained mix is well suited for compacting into near net shape VSI components having a chamfered inverted valve profile.
Example 1 A melt of 16.0 wt% Cr, 1.5 wt% Mo, 1.5 wt% W, 1 wt% V, 0.5 wt% Si, 1.5 wt% C and balance Fe was water atomised to form a pre-alloyed powder. The obtained powder was subsequently vacuum annealed at 1000 C for about 48 hours, the total annealing time being about 60 hours, after which the powder particles contained about 20% by volume of M23C6-type carbides of an average grain size of about 10 pm and about 5% by volume of M,C3-type carbides of an average grain size of about 3 pm in a ferritic matrix.
The obtained powder (hereafter referred to as OB1) was mixed with 0.5 wt% graphite and 0.75 wt% of an evaporative lubricant. The mix was compacted into test bars at a pressure of 700 MPa. The obtained samples were sintered in an atmosphere of 90N2/10H2 at a temperature of 1120 C.
After sintering the samples were subjected to cryogenic cooling in liquid nitrogen followed by tempering at 550 C.
A similar mix based on the known HSS powder M3/2, was prepared and test bars were produced using the same process as the one described above.
The test bars were subjected to hardness tests according to the Vickers method. Hot hardness was tested at three different temperatures (300/400/500 C). The results are summarised in the table below.
Powder Porosity HVO.025 HV5 Hot hardness (HV5) in mix (%) 300 C 400 C 500 C
The microstructure of the OB1 test material (see Figure 1) consists of the desired mixture of large and small carbides in a martensitic matrix. The reference material has similar microstructure (see Figure 2) but with smaller carbides than the OB1 material.
The OB1 material has somewhat higher porosity than the M3/2 material, which explains why the OB1 hardness values (HV5) are lower than those for M3/2 although the OB1 microhardness is higher than that for M3/2.
In the production of PM VSI components, the porosity is normally eliminated by copper infiltration during sintering and such effects can therefore be neglected. In the light of this, the hardness values of the OB1 material are comparable to those of the reference M3/2 material, which gives good indication that the materials should have comparable wear resistance.
Especially, maintaining hardness at elevated temperatures is important for wear resistance in VSI applications. The hot hardness test results show that the OB1 material meets these requirements.
After sintering the samples were subjected to cryogenic cooling in liquid nitrogen followed by tempering at 550 C.
A similar mix based on the known HSS powder M3/2, was prepared and test bars were produced using the same process as the one described above.
The test bars were subjected to hardness tests according to the Vickers method. Hot hardness was tested at three different temperatures (300/400/500 C). The results are summarised in the table below.
Powder Porosity HVO.025 HV5 Hot hardness (HV5) in mix (%) 300 C 400 C 500 C
The microstructure of the OB1 test material (see Figure 1) consists of the desired mixture of large and small carbides in a martensitic matrix. The reference material has similar microstructure (see Figure 2) but with smaller carbides than the OB1 material.
The OB1 material has somewhat higher porosity than the M3/2 material, which explains why the OB1 hardness values (HV5) are lower than those for M3/2 although the OB1 microhardness is higher than that for M3/2.
In the production of PM VSI components, the porosity is normally eliminated by copper infiltration during sintering and such effects can therefore be neglected. In the light of this, the hardness values of the OB1 material are comparable to those of the reference M3/2 material, which gives good indication that the materials should have comparable wear resistance.
Especially, maintaining hardness at elevated temperatures is important for wear resistance in VSI applications. The hot hardness test results show that the OB1 material meets these requirements.
Example 2 A melt of 14,5 wt% Cr, 1.5 wt% Mo, 2.5 wt% W, 1 wt% V, 0.5 wt% Si, 1.5 wt% C and balance Fe was water atomised to form a pre-alloyed powder.
The obtained powder was subsequently vacuum annealed at 1000 C for about 48 hours, the total annealing time being about 60 hours, after which the powder particles contained about 20% by volume of M23C6-type carbides of an average grain size of about 10 pm and about 5% by volume of M,C3-type carbides of an average grain size of about 3 pm in a ferritic matrix.
Processing this powder, mixed with 0.5 wt% graphite and 0.75 wt% of an evaporative lubricant, to produce test bars in the same way as in example 1, resulted in a microstructure very similar to that in Figure 1.
The obtained powder was subsequently vacuum annealed at 1000 C for about 48 hours, the total annealing time being about 60 hours, after which the powder particles contained about 20% by volume of M23C6-type carbides of an average grain size of about 10 pm and about 5% by volume of M,C3-type carbides of an average grain size of about 3 pm in a ferritic matrix.
Processing this powder, mixed with 0.5 wt% graphite and 0.75 wt% of an evaporative lubricant, to produce test bars in the same way as in example 1, resulted in a microstructure very similar to that in Figure 1.
Claims (18)
1. An annealed pre-alloyed water atomised iron-based powder, comprising:
10- below 18% by weight of Cr;
0.5-5% by weight of each of at least one of Mo, W, V and Nb;
and 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C;
wherein the iron-based powder has a matrix comprising less than 10% by weight of Cr, and wherein the iron-based powder comprises large chromium carbides and smaller and harder chromium carbides.
10- below 18% by weight of Cr;
0.5-5% by weight of each of at least one of Mo, W, V and Nb;
and 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C;
wherein the iron-based powder has a matrix comprising less than 10% by weight of Cr, and wherein the iron-based powder comprises large chromium carbides and smaller and harder chromium carbides.
2. An iron-based powder according to claim 1, including large chromium carbides having an average size of 8-45 µm and smaller and harder chromium carbides having an average size less than 8 µm.
3. An iron-based powder according to claim 1, including large chromium carbides having an average size of 8-30 µm and smaller and harder chromium carbides having an average size less than 8 µm.
4. An iron-based powder according to any one of claims 1-3, comprising 10-30% by volume of large chromium carbides and 3-10% by volume of smaller and harder chromium carbides.
5. An iron-based powder according to any one of claims 1-4, wherein the matrix is not stainless.
6. An iron-based powder according to any one of claims 1-5, wherein the powder further comprises 0-2% Si.
7. An iron-based powder according to any one of claims 1-6, having a weight average particle size of 40-100 µm.
8. An iron-based powder according to any one of claims 1-7, comprising of 12- below 18% by weight of Cr, 1-3 wt% of Mo, 1-3,5 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
9. An iron-based powder according to any one of claims 1-7, comprising 12- below 15% by weight of Cr, 1-2 wt% of Mo, 2-3 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
10. An iron-based powder according to any one of claims 1-7, comprising 14-below 18 weight of Cr, 1-2 wt% of Mo, 1-2 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
11. An iron-based powder according to claim 1, wherein the large chromium carbides are of M23C6-type, where M = Cr, Fe, Mo, W.
12. An iron-based powder according to claim 1, wherein the smaller and harder chromium carbides are of M7C3-type where M = Cr, Fe, V.
13. A method of producing an iron-based powder comprising a matrix having less than 10% by weight of Cr comprising:
subjecting an iron-based melt including 10- below 18% by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb and 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C to water atomisation in order to obtain iron-based powder particles; and annealing the powder particles at a temperature, and for a period of time, sufficient for obtaining large chromium carbides and smaller and harder chromium carbides within the particles.
subjecting an iron-based melt including 10- below 18% by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb and 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C to water atomisation in order to obtain iron-based powder particles; and annealing the powder particles at a temperature, and for a period of time, sufficient for obtaining large chromium carbides and smaller and harder chromium carbides within the particles.
14. A pressed and sintered component produced from at least a powder according to claim 1.
15. A pressed and sintered component according to claim 14; wherein a part of the C- content is alloyed during sintering.
16. A pressed and sintered component according to claim 14; wherein the pressed and sintered component is produced from a powder composition comprising the powder according to claim 1 and at least one of an iron-based powder, graphite, an evaporative lubricant, a solid lubricant, a machinability enhancing agent.
17. A pressed and sintered component according to any of claims 14-16, wherein the pressed and sintered component is a valve seat insert.
18. A pressed and sintered component according to claim 17, comprising a chamfered mating surface having an inverted valve profile formed during compaction.
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CN101590524B (en) * | 2009-06-23 | 2013-11-20 | 诸城市同翔机械有限公司 | Material formulation for high-strength powder metallurgy valve guide pipe |
AU2012362827B2 (en) | 2011-12-30 | 2016-12-22 | Scoperta, Inc. | Coating compositions |
CN104039484B (en) | 2012-01-05 | 2016-12-07 | 霍加纳斯股份有限公司 | Metal dust and application thereof |
CN102660709A (en) * | 2012-04-24 | 2012-09-12 | 邓湘凌 | High-strength wear-resisting alloy and preparation method thereof |
DK3084029T3 (en) | 2013-12-20 | 2019-11-25 | Hoeganaes Ab Publ | PROCEDURE FOR MANUFACTURING A SINTERED COMPONENT AND A SINTERED COMPONENT |
DE102015213706A1 (en) * | 2015-07-21 | 2017-01-26 | Mahle International Gmbh | Tribological system comprising a valve seat ring and a valve |
US10105796B2 (en) | 2015-09-04 | 2018-10-23 | Scoperta, Inc. | Chromium free and low-chromium wear resistant alloys |
JP7116495B2 (en) * | 2017-03-14 | 2022-08-10 | ヴァンベーエヌ コンポネンツ アクチエボラグ | High carbon cobalt alloy |
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