Source: https://patents.google.com/patent/EP0910680A1/en
Timestamp: 2019-03-24 20:02:48
Document Index: 658823138

Matched Legal Cases: ['art 20', 'art 52', 'art 50', 'art 50', 'art 50', 'art 50', 'art 50', 'art 50']

EP0910680A1 - High density forming process with ferro alloy and prealloy - Google Patents
High density forming process with ferro alloy and prealloy
EP0910680A1
EP0910680A1 EP19960942216 EP96942216A EP0910680A1 EP 0910680 A1 EP0910680 A1 EP 0910680A1 EP 19960942216 EP19960942216 EP 19960942216 EP 96942216 A EP96942216 A EP 96942216A EP 0910680 A1 EP0910680 A1 EP 0910680A1
EP19960942216
Lawcock Roger
1996-05-15 Priority to US644978 priority
1996-12-24 Application filed by Stackpole Ltd filed Critical Stackpole Ltd
1996-12-24 Priority to PCT/CA1996/000879 priority patent/WO1997043458A1/en
1999-04-28 Publication of EP0910680A1 publication Critical patent/EP0910680A1/en
A method for making a high density powdered metal article is provided. The composition consists of iron based powder, lubricant, graphite and ferro alloy additions. Satisfactory results may also be achieved by using prealloyed molybdenum grades of metal powders. The composition is compacted in rigid tools at ambient temperature, sintered at high temperature and then formed in rigid tools comprising a clearance (22) for movement of the sintered compact to final shape, at 40 to 90 tons per square inch to a density greater than 94 % of theoretical. The high density article is then annealed. The final article demostrates remarkable mechanical properties which are atypical of powdered metal components and approach those of wrought steel.
The invention relates to methods of forming sintered compacts of low alloy steel composition to high density at ambient temperature. The invention further relates to specific compositions of iron based powder metal sintered compacts which may be formed to high density, as well as the possible utilization of prealloyed molybdenum powder metals.
For a process to be of commercial value and offer a significant improvement in durability of the sintered powdered part the method of producing high density sintered powder metal parts should meet the following criteria: use low cost raw materials be suited to high volume production rates produce articles of high precision have acceptable tool life characteristics produce articles with a density in the range of 94% to 98% theoretical full density of wrought iron (equivalent to a range of 7.4 to 7.7 g/cc for low alloy compositions).
The use of a prealloyed powder is discussed by Yoshiaki et al in the SAE Technical Paper Series, given at the International Congress and Exposition in Detroit, Michigan on February 27-March 3, 1989, which is entitled "Improvement Of The Rolling Contact Fatigue Strength of Sintered Steel for Transmission Component" . However, the base iron powder utilized herein has a lower cost. Moreover Yoshiaki does not teach the use of prealloyed molybdenum powder metal to produce powder metal parts having high density and ductility.
It is another aspect of this invention to produce a method of forming sintered powder metal article by blending carbon; at least one ferro alloy powder selected from the group of ferro chromium, ferro manganese, ferro molybdenum, and a lubricant, with iron powder to form a blended mixture; pressing the blended mixture to form the article; sintering the article at a temperature greater than 1250°C; forming the sintered article in a closed die cavity having a clearance so as to produce a formed sintered powder metal part having a compressed length which is approximately 3 to 19% less than the original length when subjected to a pressure between 40 and 90 tons per square inch so as to increase the density of the formed sintered article; annealing the formed sintered article at a temperature greater than 800 °C in a reducing or carburizing atmosphere or vacuum.
It is a further aspect of this invention to provide a method of making a high density sintered powder metal article, comprising the steps of blending iron powder with ferro alloys, graphite and lubricant to provide a selected chemical composition for the finished article having at least one of the following: 0 to 0.5% carbon, 0 to 1.5% manganese, 0 to 1.5% molybdenum and 0 to 1.5% chromium and the remainder iron powder with unavoidable impurities; compacting the metal powder mixture in a rigid die to a density of approximately 90% of theoretical full density; sintering the compacted article at a temperature greater than 1250°C in a reducing atmosphere or vacuum; forming the sintered article in rigid tools at pressure in the range of 40 to 90 tons per square inch to a density in excess of 94% of theoretical full density by axial compression allowing radial expansion to decrease the axial length of the sintered article by approximately 3 to 30% of the original axial length; annealing the high density article at a temperature greater than 800 °C in a reducing or carburizing atmosphere or vacuum, where the total alloy composition is between 0 to 2.5% by weight to the total weight of sintered powder metal article.
It is another aspect of this invention to provide a method of forming sintered powder metal articles by blending carbon and lubricant with a prealloyed molybdenum powder, pressing said blended mixture to form said article, sintering said article at a temperature of at least 1100°C, forming the sintered powder metal article in a closed die cavity having a clearance for movement of said sintered powder metal to final shape with increased density, after compression wherein the formed sintered powder metal article has a compressed length which is 3 to 30% less than the original length.
Yet another aspect of this invention relates to a formed sintered powder metal article having up to 0.5% by weight Carbon, up to 1.5 % by weight Mn with the remainder being iron and unavoidable impurities and having approximately 23 % elongation and density greater than 7.4 g/cc.
Figure 1 is a cross sectional view of the forming process.
Figure 2 is a cross sectional view of the forming process for a sintered ring.
Figure 3 is a graph of the high density forming of Fe- C-Mn test bars.
Figure 4 is a graph of the high density forming of a clutch plate.
Figure 5 is a graph of formed density and closure of Fe- C-Cr rings formed at 60 tsi.
Figure 6 is a graph of formed density and closure of Fe- C-Mo rings formed at 60 tsi.
Figure 7 is a graph of formed density and closure of Fe- C-Mn rings formed at 60
Figure 8 is a graph of strength versus percent alloy in iron. Figure 9 is a graph of hardenability versus percent alloy in iron.
Figure 10 is a graph of elongation of Fe-C-Mn tensile specimens with different heat treatments.
Figure 11 is a graph of tensile strength of Fe-C-Mn specimens with different heat treatments.
Figure 12 is a high density forming property comparison.
Figure 13 is a graph of the high density forming of FeCMo Rings using a prealloyed molybdenum powder such as QMP4401 having 0.85 Mo prealloy and adding 0.2% C with the remainder essentially Fe and unavoidable impurities. The graph shows the relationship of formed density to forming pressure for QMP 4401 0.85% Mo prealloy + 0.2% C.
Figure 14 is a cross sectional view of the forming process for a multi-level component.
Figure 15 is a graph showing the effect of forming pressure on density of a sintered powder metal article having 0.2% C, 0,9% Mn, 0.5 % Mo with the remainder being iron and unavoidable impurities.
The present invention describes a method of forming sintered powder metal compacts to a density in the range of 7.4 to 7.7 g/cc. The compositions of the final articles are of a low alloy steel distinction where the carbon content is less than 0.5% and preferably less than 0.3 % by weight of the sintered article and have formable characteristics. The forming is preferably carried out at ambient temperatures (although elevated temperatures could be used) which provides acceptable tooling life and excellent precision features. The process utilizes low cost iron powders which are blended with calculated amounts of ferro alloys, graphite and lubricant such that the final desired chemical composition is achieved and the powder blend is suited to compaction in rigid compaction dies. The process is generally described in U.S. Patent 5,476,632.
Alternatively it has been found that the benefits of the invention to be described herein may be arrived at by using prealloyed molybdenum powder metals in which case such materials can be sintered at conventional sintering temperatures of 1100°C to 1150°C , or alternatively at high temperature sintering at greater than 1250°C.
Sintering of the ferro alloy compositions is undertaken at high temperatures generally greater than 1250°C such that oxides contained within the compact are reduced. No significant densification occurs during the sintering process. The density of the sintered compact will still be around 90% of theoretical.
(a) sizing - which may be defined as a final pressing of a sintered compact to secure a desired size or dimension;
(b) coining - which can be defined as pressing a sintered compact to obtain a definite surface configuration;
(c) repressing - which can be defined as the application of pressure to a previously pressed and sintered compact, usually for the purpose of improving physical or mechanical properties and dimensional characteristics;
(d) restriking - additional compacting of a sintered compact.
The compositions of the powdered metal articles that are the subject of this invention are of the kind not generally employed in the powdered metal industry. Prior art compositions generally mcluded the use of alloys consisting of iron, carbon, copper, nickel and molybdenum. In this invention, alloys of iron, such as manganese, chromium and molybdenum are used and are added as ferro alloys to the base iron powder as described in U.S. patent 5,476,632, which is incorporated hereby by reference. Carbon may also be added. The alloying elements ferro manganese, ferro chromium, and ferro molybdenum may be used individually with the base iron powder, or in any combination, such as may be required to achieve the desired functional requirements of the manufactured article. In other words two ferro alloys can be used or three ferro alloys can be blended with the base iron powder. Examples of such base iron powder includes Hoeganaes Ancorsteel 1000/1000B/1000C, Quebec Metal Powder sold under the trade marks QMP Atomet 29 and Atomet 1001.
The base iron powder composition consists of commercially available substantially pure iron powder which preferably contains less than 1 % by weight unavoidable impurities. Additions of alloying elements are made to achieve the desired properties of the final article. Examples of compositional ranges of alloying elements that may typically be used include at least one of the following: 0 to 0.5% carbon, 0 to 1.5% of manganese, 0 to 1.5% chromium and 0 to 1.5% of molybdenum where the % refers to the percentage weight of the alloying element to the total weight of the sintered product and the total weight of the alloying elements is between 0 to 2.5%. The alloying elements Mn, Cr, and Mo are added as ferro alloys namely FeMn, FeCr, FeMo. The particle size of the iron powder will have a distribution generally in the range of 10 to 350 μm. The particle size of the alloying additions will generally be within the range of 2 to 20 μm. To facilitate the compaction of the powder a lubricant is added to the powder blend. Such lubricants are used regularly in the powdered metal industry. Typical lubricants employed are regular commercially available grades of the type which include, zinc stearate, stearic acid or ethylene bistearamide.
Alternatively prealloyed molybdenum powder metal having molybdenum compositions of 0.5 % to 1.5 % with the remainder being iron and unavoidable impurities can be used. Prealloyed molybdenum powder metal is available from Hoeganaes under the designation Ancorsteel 85HP (which has approximately 0.85% Mo by weight) or Ancorsteel 150HP (which has approximately 1.50% by weight Mo) or Quebec Powder Metal under the trademarks QMP at 4401 (which has approximately 0.85% by weight Mo). The particle size of the prealloyed molybdenum powder metal is generally within the range of 45μm to 250μm typically. The same type lubricants as referred to above may be used to facilitate compaction. Carbon may also be added between 0 to 0.5% by weight.
The compacted article is then sintered at high temperature, in excess of 1250°C while a reducing atmosphere or a vacuum is maintained around the article. In the case of the prealloyed molybdenum powder metal such material can be sintered at conventional sintering temperatures of 1100°C to 1150°C or at the higher temperature up to 1350°C. In the sintering process, contacting particle boundaries become metallurgically joined and impart strength and ductility to the sintered article. In addition, the reducing atmosphere causes a reduction of oxides from both the iron powder and the alloying element additions. The chemical reduction process provides for clean particle surfaces which enhance the metallurgical bonding of the particles, and most importantly, allows for uniform diffusion of the alloying elements into the iron particles. The final sintered article will then contain a homogeneous or near homogeneous distribution of alloying elements throughout the microstructure. A sintering method, or choice of alloying which promotes a non homogeneous microstructure is considered to be undesirable. A non homogeneous microstructure will contain a mixture of hard and soft phases which will adversely affect the forming characteristics of the sintered article.
The closed die cavity of the forming operation is shown in Figure 1. The closed rigid die cavity 10 is defined by spaced vertical die walls 12 and 14, lower punch or ram walls 16 and upper punch or ram 18. The sintered part is represented by 20. During the forming operation upper punch or ram 18 imparts a compressive force to sintered part 20. Alternatively the compressive force can be imparted by relative movement between lower punch or ram wall 16 and upper punch or ram wall 18. The closed die cavity is designed with a clearance 22 to permit movement of the ductile sintered material in a direction perpendicular to or normal to the compressive force as shown by arrow A. During compression the overall compressed length or height of the sintered article is reduced by the dimension S.
Conventional coining may permit reduction or movement of the sintered material in direction A by 1 to 3 % . The invention described herein permits movement of the sintered material beyond 3 % of the original height or length. It is possible as shall be described herein that the reduction S or percentage closure of the sintered material can reach as much as 30% reduction of dimension H. Particularly advantageous results are achieved by having a closure which represents a compressed length or height Ch, which is between 3% to 19%, less than the original uncompressed length. In other words S represents the change in the overall height H of the sintered part to that of the compressed height Ch. Moreover, the compression of the overall length or height collapses the microstructural pores in the sintered powder metal part and thereby densifies the sintered part.
Another example of the closed die cavity is shown in Figure 2 where the closed rigid die cavity 10 is again defined by the rigid tools namely spaced vertical die walls 12 and 14 respectively, the lower punch or ram wall 16 and upper punch or ram wall 18 and core 19. The core 19 moves in sliding coaxial relationship within aligned holes formed in upper punch or ram and lower punch or ram. In this case the sintered part is represented by a ring 21 which has a bore 23 therethrough. Again during the forming operation upper punch or ram 18 imparts a compressive force A to the sintered ring 21. Alternatively the compressive force can be imparted by relative movement between lower punch or ram wall 16 and upper punch or ram 18. The closed die cavity is once again designed with a clearance 22 to permit movement of ductile sintered material in a direction perpendicular or normal to the compressive force A. Once formed or compressed the sintered material will move within the closed cavity from the position of the arrows Cv, Ch to Dv and Dh. In other words, the sintered material will move to fill the clearance 22 . Upon compression the bore 23 will have a smaller internal diameter after the application of the compressive force. The compressed height of the sintered ring 21 can be reduced by approximately 3 to 19% of the uncompressed height. In the case shown in Figure 2, the height of the ring also represents the height is in the axial direction of the ring. In other words the sintered article is formed by axial compression allowing radial expansion to decrease the axial length of the sintered article by approximately 3 to 30% of the original axial length.
The invention described herein may be used to produce a variety of sintered powder metal powder articles or parts which have multi-levels. Figure 14 is a cross sectional view of the forming process for a multi-level component such as for example a transmission sprocket 50. The transmission sprocket 50 shown in Figure 14 is cylindrical in shape with Figure 14 being a cross sectional therethrough. The sprocket has a hub portion 52, a disc shaped portion 54 and tooth portion 56.
A multi-level component is comprised of the powder metal powders referred to earlier namely: (a) blending carbon, at least one ferro alloy selected from the group of Ferro Molybdenum, Ferro Chromium and Ferro Manganese, a lubricant with iron powder and unavoidable impurities as the remainder, or (b) blending Carbon and lubricant with a prealloyed molybdenum powder as referred to earlier
The upper punches may include a number of punches depending on the configuration of the multi-level part and in the example shown in Figure 4 comprises three separate moveable punches 70, 72 and 74. The upper punches 70, 72 and 74 may comprise cylindrically shaped punches which are adapted for sliding movement relative to one another in a close tolerance relationship.
A clearance 76 is provided between the hub 52 and upper punch 72 with another clearance 78 provided between the die 66 and the tooth section 56 . Figure 14 illustrates that there is no clearance between the core 64 and the part 52 between lower punch 60 and upper punch 74; although a clearance could be provided in this area if required.
The tool set 58 shown in Figure 14 shows the sintered multi-level part 50 in the rigid tool set 58 in a closed position. The sintered powder metal part 50 would be introduced into the tool set 58 when the upper punches 70, 72 and 74 are retracted sufficiently away from lower punch 60 and core 64 to an open position so as to permit the introduction of a multi¬ level sintered part 50 into the tool set 58. The die 66 could also be retracted in an upper position with the upper dies or in a lower position closer to the lower punch when the tool set 58 is in an open position. Such die 66, core 64, lower punch 60 and upper punches 70, 72, and 74 may be moved in a press (not shown) in a manner well known to those persons skilled in the art such has by utilizing cylinders, rams or punch holders.
Accordingly, once the multi-layered part 50 is introduced into the tool set 58 the lower punch 60, die 66, core 64 and upper punches 70, 72 and 74 move in relative sliding movement so as to present a closed die cavity shown in Figure 14. The closed die cavity has clearance 76 and 78 so as to produced a formed sintered powder metal multi-level part 50 having a compressed length Ch which is approximately 3 to 30% less than the original length H so as to increase the density of said formed sintered multi-layered part 50. In the example shown in Figure 14 the clearance 76 is located in the hub area 52 while clearance 78 is located in the tooth area 56. Accordingly the distance H or axial length of the hub 52 or the distance H of the tooth 56 will be reduced after compression between 3 to 30% in accordance with the teachings of this invention. The actual percentage shortening of the length of the hub 52 and teeth 56 in the axial direction 80 may either be the same or may be in different percentages depending on the amount of clearance 76 and 78. Moreover the thickness or axial length of the disc 54 may remain the same before forming and after forming in which event the relative movement of lower punch 60 and upper punch 72 will remain constant during forming. Alternatively, upper punch 72 and lower punch 60 may move relatively towards one another so as to permit reduction of the disc section 54 sintered material in the direction A by 1 to 3 percent as in the case of conventional forming. Reduction of 3 to 30% may also be achieved in section 54.
Mn 0 - 1.5%
Cr 0 - 1.5%
Mo 0 - 1.5%
C 0 - 0.5%
Fe and unavoidable impurities remainder
In other examples, at least one alloying element will be selected from the group of FeMn, FeCr, FeMo, and then blended with carbon and a lubricant substantially pure iron powder so as to produce a sintered part having a total alloy composition (i.e. Mn, Cr, Mo, C) of up to 2.5 % by weight of the total weight of the sintered part with the individual alloying elements having the following percent composition to total weight of the sintered part:
Cr 0 - 1.5 %
Mo 0 - 1.5% C 0 - 0.5 %
Example - Ferroalloy
Carbon, a ferro alloy such as ferro manganese, is blended with lubricant and iron powder. An example of iron powder used is Hoeganaes Ancorsteel 1000/lOOOB/lOOOC or QMP Atomet 29 or QMP Atomet 1001. By way of example Mn may be added as FeMn, which contains 71 % Mn. The particle size of the FeMn will generally be within the range of 2 to 20 μm.
The iron powder is substantially pure iron powder with preferably less than 1 % of unavoidable impurities. The particle size of the iron powder will have a distribution range of 10 to 350μm. Lubricant used may be zinc stearate. The blended mixture is compacted in a press with compacting pressure of about 40 tons per square inch to produce a green compact with a density of approximately 90% of theoretical. The compacted part is then sintered at a temperamre greater than 1250°C for a time duration of approximately 20 minutes. Sintering can occur at a temperature between 1250°C and 1380°C. The quantity of carbon, ferro manganese and iron powder is selected so as to produce a sintered powder metal part having the following composition by weight to the weight of the total sintered part namely:
Mn 0.7%
The sintered part is then formed as previously described in a closed die cavity which defines the final net shape part. The closed die cavity will have a clearance designed for movement of the ductile sintered powder metal to collapse the pores and thereby increase the density of the formed sintered powder metal part. Example - Prealloy
Good results have also been achieved by using prealloyed molybdenum powder having a total molybdenum content of between 0.5 % to 1.5% by weight in the prealloyed form as shown in Figure 13.
Apparent density 2.92g/cm3 Flow 26 seconds/50g Chemical analysis C 0.003%
O 0.08%
S 0.007%
Mo 0.85%
Ni 0.07%
Si 0.003%
Fe greater than 98%
Other grades such as Hoeganaes Ancorsteel 85HP (which has approximately 0.85% Mo by weight) or Ancorsteel 150HP (which has approximately 1.50% by weight of Mo) and QMP AT 4401 (which has approximately 0.85% by weight of Mo) can be used. The particle size of the prealloyed powder will generally fall within the range of 45μm to 250μm typically.
The prealloyed molybdenum powder is blended with lubricant and 0 to 0.5% by weight of carbon to total weight of sintered powder metal, and then compacted as described above to produce a green compact with a density of approximately 90% of theoretical density of wrought iron. The compacted article is then sintered at either conventional sintering temperatures of 1100°C to 1150°C or could alternatively be sintered at a higher temperature up to 1350°C for a time duration of approximately 20 minutes.
Figure 3 shows the forming or coining of sintered powder metal test bars produced as shown in Figure 1 having a carbon and manganese content. Figure 3 shows that when the test bar is subject to an increase in the coining or forming pressure between 40 and 75 tons per square inch the formed sintered part will have a resultant increase in density of approximately 7.25 to just over 7.50 g/cm3. In other words with an increase in forming pressure an increase in formed density occurs. The density of the Fe-C-Mn test bars will approach the theoretical density of wrought steel. In the examples outlined herein forming occurs at ambient temperature although in another embodiment forming could occur at an elevated temperamre.
Figure 4 is a chart that shows the impact of forming pressure to the formed density of a sintered part comprised of Fe-C-Mn. Figure 4 generally illustrates that with an increase in forming pressure an increase in formed density will be observed as illustrated therein.
Figure 5 illustrates formed density and closures for Fe- C-Cr powder metal parts which are coined at 60 tons per square inch. The first bar graph to the left shows that a sintered powder metal part having 0.48% chromium and 0.16% carbon with the remainder being essentially iron and unavoidable impurities when formed or coined at 60 tons per square inch produces a formed sintered part having a density of over 7.65 g/cc. The closure or the amount of reduction S of the compressed height verses the uncompressed height of the sintered ring approaches approximately 30% . In other words, the inside diameter of the ring 21 was sufficiently large and the clearance designed so as to produce a closure or reduction of almost 30% in the compressed height verses the uncompressed height of the formed sintered ring. The second bar graph illustrates a sintered part having 1.15% chromium to 0.15% carbon to the total weight of the sintered part which is formed at 60 tons per square inch so as to produce a formed sintered part having a density of approximately 7.625 g/cc. The closure or the reduction in the height S of the same sized ring 21 is slightly lower at 28%.
The third bar graph shown in Figure 5 shows a sintered part having 1.51 % chromium and 0.15 % carbon with the remainder being iron and unavoidable impurities which has been formed at 60 tons per square inch so as produce a part having a density of approximately 7.525 g/cc. The closure is approximately 25 % . Three other results are also shown in Figure
Figure 6 is another graph showing the formed density and closure of Fe-C-Mo powder metal which has been coined at 60 tons per square inch. Generally speaking, higher concentrations of molybdenum will decrease the density of the formed part as well as provide a smaller degree of closure. For example, a sintered part having 0.41 % by weight of molybdenum and 0.09% carbon with the remainder being iron once formed at 60 tons per square inch produces a part having a density of slightly greater than 7.60 g/cc. Closure is approximately 28% .
Figure 7 illustrates the formed density and closure Fe-C-Mn powder metal formed at 60 tons per square inch. Generally speaking higher concentrations of manganese reduce the density of the formed sintered part and permit less closure.
The foregoing shows that by controlling the chemical composition of the sintered article, and by controlling the pressing forces and clearance in a closed die cavity, a remarkable increase in density can be achieved. Figures 3 to 7 show the densities and closures that can be achieved when using singular combinations of the ferro alloys namely FeMo, FeCr and FMn with base iron powder. It is of course possible as described above to use more than one ferro alloy, ie FeMo, FeCr, FeMn with base iron powder as desired to achieve functional requirements of the manufactured article. For example, Figure 15 shows that increased formed densities can be achieved with 0.2% C, 0.9% Mn and 0.5 % Mo by weight. In this example FeMn and FeMo is added and blended with the base iron powder and carbon so as to produce a sintered part having 0.2% C, 0.9% Mn and 0.5% by weight to the total weight with the remainder being iron and unavoidable impurities. In other words separate ferro alloys of FeMo, FeCr and FeMn may be admixed with base iron powder.
Figures 8 and 9 generally show the effect that the percentage of the alloyed ingredients Mn, Mo, Ni and Cr has on the strength and hardenability of the sintered part.
Figure 8 shows that the addition of manganese has a greater effect on the tensile strength of the metal powder metal part than molybdenum, chromium or nickel.
Figure 9 generally shows that manganese increases the hardenability of the sintered powder metal articles more than molybdenum. The addition of molybdenum has a greater effect on the hardenability of the sintered powder metal part than chromium or nickel. Furthermore one should be careful not to add a lot of manganese as this may hinder the forming operation as Mn has a strong effect on the strength. In particular no more than 1.5% of Mn should be included in the total weight of the sintered powder metal article. For example, one may use Cr since at a given composition Cr does not increase the strength of the sintered article as much as Mn (see Figure 8) but does impart high hardenability (see Figure 9).
Subsequent to the forming operation, in order to develop the full mechanical properties of the article, it may be necessary to subject the article to a heat treatment operation. The heat treatment operation is generally carried out within the temperature range of 800 °C to 1300°C. The attached figures 10 and 11 indicate the effect of heat treatment conditions on the final mechanical properties of the article. The conditions may be varied within the above range to suit the desired functional requirements of the specific article. It is also preferable to use a protective atmosphere during the annealing process. The atmosphere prevents oxidization of the article during the exposure to the elevated temperature of the heat treatment process. The actual atmosphere used may consist of hydrogen/ nitrogen blends, nitrogen/exothermic gas blends, nitrogen/endothermic gas blends, dissociated ammonia or a vacuum. In the heat treatment stage it is generally preferable to maintain a neutral atmosphere in terms of carbon potential with respect to the carbon content of the article. In special instances, for example should the article require high wear resistance, a carburizing atmosphere may be used during heat treatment. The carburizing atmosphere may consist of methane or propane where the carbon atoms will migrate from the methane or propane to the surface layers of the article. In such an operation, carbon will be introduced into the surface layers of the article. If the article is subsequently quenched, a case hardened product can be produced with beneficial wear resistant properties.
After the heat treatment, the article is ready for use and will exhibit mechanical properties that are generally very similar to wrought steel of the same chemical composition. Figure 12 shows typical mechanical properties of a material manufactured by the invented process. The remarkable ductility, impact strength and fatigue strength to tensile strength ratio are a typical consequence of the new process. As can be seen froni the comparative chart for regular PM materials (represented by the designation FC0200), which are typically manufactured to around 90% of theoretical density, the previously described mechanical properties are significantly improved. For example Figure 12 shows the mechanical properties of a Fe C Mn (0.2C and 0.7Mn) produced by the invention described herein versus the mechanical properties of a regular PM material such as FC0200 (having a low carbon 0-0.3% C and low alloy material i.e. 1.5 to 3.9% by weight copper) versus the mechanical properties of wrought steel having the designation AISI 1020. The unnotched impact strength of Fe C Mn at greater than 120 ft lb and the elongation at 23 % are notable. Fatigue properties were determined by three point bending. The high density also produces a significant improvement in elastic modulus. The elongation achieved is dependent on the alloy content and density of the final part.
CLAIMSThe embodiments of the invention in which an exclusive property or privilege is claimed are defmed as follows:
1. A method of forming sintered powder metal articles to a high density by forming the sintered powder metal in a closed die cavity having a clearance for movement of said sintered powder metal to final shape with increased density after compression wherein the formed sintered powder metal part has a compressed length which is approximately 3 to 30% less than the original length.
3. The method of claim 2 wherein said sintered formed powder metal part has a total alloy composition between 0 to 2.5% by weight to the total weight of sintered metal article, with the individual alloying elements having the following percent composition to the total weight of the sintered part: Mn 0 - 1.5%; Cr 0 - 1.5% ; Mo 0 - 1.5%; C 0 - 0.5%; Fe and unavoidable impurities being the remainder.
(ii) at least one ferro alloy selected from the group of ferro molybdenum, ferro chromium and ferro manganese; (iii) a lubricant, with (iv) iron powder.
(b) pressing said blended mixmre to form said article
(c) sintering said compact at a temperature greater than 1250°C.
(ii) at least one ferro alloy powder selected from the group of ferro chromium, ferro manganese, ferro molybdenum, and (iii) a lubricant, with (iv) iron powder to form a blended mixmre;
(b) pressing said blended mixmre to form said article;
(c) sintering said article at a temperamre greater than 1250°C;
(d) forming said sintered article in a closed die cavity having a clearance so as to produce a formed sintered powder metal part having a compressed length which is approximately 3 to 19% less than the original length when subjected to a pressure between 40 and 90 tons per square inch so as to increase the density of said formed sintered article;
(e) annealing said formed sintered article at a temperamre greater than 800°C in a reducing or carburizing atmosphere or vacuum.
8. The method of claim 7 where said sintered powder metal has at least one alloy selected from the group of Mn, Mo, Cr, and C with a total alloy composition up to 2.5% by weight to the total weight of sintered part and the remainder of said sintered article has the following weight composition: Mn 0 - 1.5%
9. The method of claim 8 wherein said closed die cavity has a clearance so as to permit said sintered powder metal to move within said closed die cavity where said sintered powder metal part is compressed so as to reduce the sintered length of said article between 3 to 19%.
Fe and unavoidable impurities being the remainder.
13. The method of claim 11 to produce a sprocket
16. A method of making a high density sintered powder metal article, comprising the steps of: (a) blending iron powder with ferro alloys, graphite and lubricant to provide a selected chemical composition for the finished article having at least one of the following: 0 to 0.5 % carbon, 0 to 1.5% manganese, 0 to 1.5% molybdenum and 0 to 1.5% chromium and the remainder iron powder with unavoidable impurities;
(b) compacting the metal powder mixmre in a rigid die to a density of approximately 90% of theoretical full density;
(c) sintering the compacted article at a temperamre greater than 1250°C in a reducing atmosphere or vacuum;
(d) forming the sintered article in rigid tools at pressure in the range of 40 to 90 tons per square inch to a density in excess of 94% of theoretical full density by axial compression allowing radial expansion to decrease the axial length of the sintered article by approximately 3 to 30% of the original axial length.
(e) annealing the high density article at a temperamre greater than 800 °C in a reducing or carburizing atmosphere or vacuum;
17. A method of forming sintered powder metal article by blending carbon and lubricant with a pre-alloyed molybdenum powder, pressing said blended mixmre to form said article, sintering said article at a temperamre of at least 1100°C, forming the sintered powder metal article in a closed die cavity having a clearance for movement of said sintered powder metal to final shape with increased density after compaction wherein the formed sintered powder metal article has a compressed length which is 3 to 30% less than the original length.
18. A method as claimed in claim 17 wherein said carbon has a composition of 0 to 0.5 % by weight of the total weight of sintered powder metal article.
19. A method as claimed in claim 18 wherein said carbon is added as graphite.
20. A method as claimed in claim 18 wherein said sintered formed powder metal article has a total molybdenum content of between 0.5% to 1.5 % by weight to the total weight of sintered metal article, with Fe and unavoidable impurities being the remainder.
21. A method as claimed in claim 20 wherein said sintering occurs at a temperamre of between 1100°C to 1150°C.
22. A method as claimed in claim 21 wherein said formed sintered powder metal article has a compressed length which is approximately 3 to 19% less than die original length.
23. A meuiod of forming sintered powder metal articles to a high density by forming the sintered powder metal in a die cavity having a clearance for movement of said sintered powder metal to final shape with increased density after compaction wherein the formed sintered powder metal part has a compressed length which is approximately 3 to 30% less than the original length.
24. A formed sintered powder metal article having up to 0.5% by weight C, up to 1.5% by weight Mn with the remainder being iron and unavoidable impurities and having approximately 23% elongation, and density greater than 7.4 g/cc.
25. A formed sintered powder metal article as claimed in claim 24 wherein said density is between 7.4 g/cc and 7.7 g/cc.
26. A formed sintered powder metal article as claimed in claim 25 having 0.2% by weight carbon and 0.7% weight Manganese.
EP19960942216 1996-05-15 1996-12-24 High density forming process with ferro alloy and prealloy Ceased EP0910680A1 (en)
US644978 1996-05-15
EP0910680A1 true EP0910680A1 (en) 1999-04-28
EP19960942216 Ceased EP0910680A1 (en) 1996-05-15 1996-12-24 High density forming process with ferro alloy and prealloy
JP5959263B2 (en) 2012-03-28 2016-08-02 日立化成株式会社 Pinion gear and a method of manufacturing the same
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2001-05-16 18R Refused