CN1049168C - Controllable casting technology for monotectic alloy antifriction bearing material - Google Patents
Controllable casting technology for monotectic alloy antifriction bearing material Download PDFInfo
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- CN1049168C CN1049168C CN94112581A CN94112581A CN1049168C CN 1049168 C CN1049168 C CN 1049168C CN 94112581 A CN94112581 A CN 94112581A CN 94112581 A CN94112581 A CN 94112581A CN 1049168 C CN1049168 C CN 1049168C
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- 239000000956 alloy Substances 0.000 title claims abstract description 94
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 93
- 238000005266 casting Methods 0.000 title claims abstract description 42
- 239000000463 material Substances 0.000 title claims abstract description 16
- 238000005516 engineering process Methods 0.000 title description 8
- 238000000034 method Methods 0.000 claims abstract description 31
- 238000001816 cooling Methods 0.000 claims abstract description 26
- 238000007711 solidification Methods 0.000 claims abstract description 7
- 230000008023 solidification Effects 0.000 claims abstract description 7
- 238000002347 injection Methods 0.000 claims abstract description 4
- 239000007924 injection Substances 0.000 claims abstract description 4
- 239000007788 liquid Substances 0.000 claims description 9
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 claims description 6
- 238000009413 insulation Methods 0.000 claims description 6
- 229910052797 bismuth Inorganic materials 0.000 claims description 5
- 230000008014 freezing Effects 0.000 claims description 5
- 238000007710 freezing Methods 0.000 claims description 5
- 229910007563 Zn—Bi Inorganic materials 0.000 claims description 3
- 238000011049 filling Methods 0.000 claims description 3
- 239000004615 ingredient Substances 0.000 claims description 2
- 230000005484 gravity Effects 0.000 abstract description 10
- 238000005204 segregation Methods 0.000 abstract description 9
- 239000012071 phase Substances 0.000 description 16
- 229910052751 metal Inorganic materials 0.000 description 10
- 239000002184 metal Substances 0.000 description 10
- 239000002245 particle Substances 0.000 description 10
- 238000002360 preparation method Methods 0.000 description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 8
- 229910002804 graphite Inorganic materials 0.000 description 8
- 239000010949 copper Substances 0.000 description 7
- 238000009826 distribution Methods 0.000 description 7
- 239000010439 graphite Substances 0.000 description 7
- 238000004519 manufacturing process Methods 0.000 description 7
- 238000009749 continuous casting Methods 0.000 description 6
- 229910000975 Carbon steel Inorganic materials 0.000 description 5
- 239000010962 carbon steel Substances 0.000 description 5
- 229910001220 stainless steel Inorganic materials 0.000 description 5
- 229910052718 tin Inorganic materials 0.000 description 5
- 239000000470 constituent Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910052745 lead Inorganic materials 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 239000010935 stainless steel Substances 0.000 description 4
- 239000011701 zinc Substances 0.000 description 4
- 229910001018 Cast iron Inorganic materials 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 239000002826 coolant Substances 0.000 description 3
- 239000007791 liquid phase Substances 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
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- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
- 229910006339 Si—Pb Inorganic materials 0.000 description 1
- WIKSRXFQIZQFEH-UHFFFAOYSA-N [Cu].[Pb] Chemical compound [Cu].[Pb] WIKSRXFQIZQFEH-UHFFFAOYSA-N 0.000 description 1
- 229910000905 alloy phase Inorganic materials 0.000 description 1
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Abstract
一种偏晶合金减磨轴承材料的铸造方法及设备，其特征在于：(1)需先将合金熔化为均匀单相熔体；(2)控制注锭速度，使注入量与凝固量相等；(3)对合金熔体预冷却；(4)对铸锭强制冷却。本发明可低成本生产匀质偏晶合金，并最大限度的减少这种合金在重力场下严重的重力偏析。
A method and equipment for casting a monotectic alloy anti-friction bearing material, characterized in that: (1) the alloy needs to be melted into a uniform single-phase melt; (2) the ingot injection speed is controlled so that the injection amount is equal to the solidification amount; (3) Pre-cooling the alloy melt; (4) Forced cooling of the ingot. The invention can produce homogeneous monotectic alloy at low cost, and minimize serious gravity segregation of the alloy under gravity field.
Description
The present invention relates to foundry engieering, a kind of foundry engieering of monotectic alloy ball-and-roller bearing material is provided especially.
Monotectic alloy is the broad-spectrum metal material of a class, topmost several monotectic alloys comprise copper base monotectic alloy (copper-lead base) at present, aluminium base monotectic alloy (as aluminium lead or aluminium bismuthino), zinc-base monotectic alloy (as zinc lead or zinc bismuthino) etc., these monotectic alloy common characteristic are a large amount of second soft phase Pb of disperse distribution on harder metallic matrix, the soft spherolite of Bi, a large amount of result of the tests show, alloy with this metallurgical structure generally has the good wear performance, so this class monotectic alloy is specially adapted to make the ball-and-roller bearing material under the different sliding conditions.
During the monotectic alloy melting and other alloy serious difference be on this binary alloy phase diagram, more than monotectic line, below the binode dotted line, there is a liquid phase immiscibility district, in this temperature range, do not mix mutually each other between each constituent element of molten metal, when these metal constituent element density have nothing in common with each other, under the terrestrial gravitation field action, the mutual again immiscible metal constituent element of different densities will separate automatically, obtain having the ingot casting of macroscopical gravity segregation feature after solidifying, this gravity segregation even can develop into the metal derby of layering when serious can not obtain alloy at all, thus with other alloy phase ratio, it is impossible utilizing conventional ingot casting technology to produce monotectic alloy, and this also is the one of the main reasons of monotectic alloy slower development.
In order to overcome the strong behavior that is separated in the preparation monotectic alloy process, produce even matter monotectic alloy material, people had once carried out long-term effort, and main method has powder metallurgic method at present, band shape continuous casting process (Zhang Baoyi, the sliding bearing of the internal-combustion engine material, China Machine Press (1989)), HIP sintering method (DE 3604861, (1986)), high speed machine paddling process (S.Mohan, etal, Z.Metallkd, 80, (1989), 904), continuous casting process (EPO440275A1, (1992), EP545607, (1993)) etc.The advantage of PM technique is the liquid phase separation tendency that overcomes monotectic alloy under the gravitational field that it can be successful; be easy to adjust the composition of monotectic alloy to obtain best bearing performance; but the shortcoming of this technology is that the density of material is lower; its strength level is also relatively low; secondly powder metallurgy requires complicated metal flouring technology; uniform powder and gas shield sintering are so manufacturing cost is higher relatively.Band shape continuous casting process production efficiency is higher, but because complex process, equipment investment is high and to shortcomings such as monotectic alloy kind sensitivities, be further improved, the high speed machine paddling process is that the employing rotating speed is 1500 rev/mins to 3200 rev/mins a high speed agitator stirring monotectic alloy melt, make it homogenising, casting then utilizes the liquid of high-speed motion to reach the purpose that suppresses gravity segregation.This technology is to be difficult to find under the high temperature do not react with Al to the main shortcoming of Al base monotectic alloy, and the material with sufficient mechanical strength and thermal-shock resistance is made the high-quality high speed agitator, and to Cu base monotectic alloy because the fusion temperature height, liquid viscosity is big, finds a kind of suitable high-temperature material difficulty more.In continuous casting technology, the method that employing is cooled off at a high speed melt suppresses the gravity segregation of the second phase drop in the melt, thereby obtain even matter monotectic alloy continuous casting billet, the main shortcoming of this technology is the restriction that is subjected to the monotectic alloy thermal conductivity, the continuous casting billet size is confined very little, simultaneously because too high cooldown rate, make in the monotectic alloy the second mutually soft particle size very tiny, this very tiny soft particle continue after the operation of rolling in, be deformed into more tiny band tissue with continuing along rolling direction, and this too tiny soft phase particle is difficult to the due advantageous effect of performance in monotectic ball-and-roller bearing material.
The object of the invention is to provide a kind of method of controlling casting, and low-cost production is spared the matter monotectic alloy, and reduces this alloy serious gravity segregation effect under gravitational field to greatest extent.
The invention provides a kind of casting method of monotectic alloy ball-and-roller bearing material, be primarily aimed at following monotectic alloy:
A.Al base monotectic alloy such as Al-Bi or Al-Pb base alloy;
B.Cu base monotectic alloy such as Cu-Pb base alloy;
C.Zn base monotectic alloy such as Zn-Bi or Zn-Pb base alloy;
It is characterized in that technical process is:
(1) at first with the monotectic alloy fusing, and is heated to above 10～250 ℃ of binode dotted line, makes it become the single-phase alloy melt of uniform ingredients;
(2) ingot speed is annotated in control, the alloy melt amount of unit interval injection ingot mould is equated, i.e. v with the amount of solidifying of ingot mould alloy
1S
1=v
2S
2, v wherein
1Be the beam speed of high-temperature fusant, v
2Be setting rate in the ingot casting (being the speed that upwards pass at solid-liquid interface in the ingot mould), S
1Be water filling port net sectional area, S
2Be ingot casting sectional area, S
1/ S
2Be controlled within 0.005～0.3 scope.
(3) the monotectic alloy melt is carried out pre-cooled, make it, be generally this alloy and begin above 5～150 ℃ of freezing point near this alloy graining point;
(4) ingot casting is forced cooling, its cooling velocity should guarantee, the ingot solidification speed v
2Between 5～15mm/s, change.
The present invention also provides the equipment that is exclusively used in said method, the bottom filling tundish (2), the ingot mould (4) that comprise heating furnace (1), band heater, it is characterized in that: the chute (3) that an available cycles water is forced cooling also is set, the angle that chute (3) and ground inclination are 5 °～80 ° between tundish (2) and ingot mould (4).
Alloy heating means of the present invention can be selected any conventional heating means such as resistance heated, heating in medium frequency or plasma heating for use, ingot speed is annotated in control of the present invention can use taper stopper method or slide gate nozzle, or fixing any conventional method such as mouth of a river, the speed of beam is controlled by the liquid level of tundish, so in annotating the ingot process, want in time in the insulation tundish, to replenish new alloy melt, make the tundish liquid level keep a stationary value.It is of the present invention that to carry out dynamically pre-cooled to the monotectic alloy melt be to force cooling and carry out with the angled special chute in ground by one, this special chute inner surface can be a tubulose, half garden or rectangle, can be with graphite or metal material such as carbon steel, cast iron, stainless steels etc. are made, the water jacket that one sealing is arranged in the outside of special chute, can (comprise water by circulating coolant, oil or gas) force to cool off, the angle on chute and ground is 5 °～80 °, optimum value is 30 °～60 °, the precooled temperature of alloy melt can be adjusted by the length of special chute, this special chute can be whole, also can be that burst is assembled.It is of the present invention that ingot casting is forced to cool off is to be undertaken by a special ingot mould, this special ingot mould can be made by graphite or carbon steel, cast iron, stainless steel and other metal materials, the Packed water jacket in the outside can be forced cooling by circulating coolant (comprising water, oil or gas).The cross section of ingot mould can be garden type, long flat type or square.The cooldown rate of ingot casting is composite factor decisions such as the wall thickness of pyroconductivity, ingot mould of internal diameter, ingot mould material according to ingot mould and circulating coolant, can calculate by heat transfer theory the freezing rate of ingot casting is controlled within 5～15mm/s scope.Less when the ingot casting size, ingot mould itself conducts heat better, and thermal capacity is bigger, when the ingot casting cooldown rate can guarantee above-mentioned freezing rate scope, also can use the common metal mould or the above-mentioned special ingot mould of graphite mo(u)ld replacement of optional cooling.The cooling capacity of ingot mould should be controlled the notes ingot speeds match of casting with what is called, the ingot mould cooling capacity is too fast, annotate the ingot underspeed and will in ingot casting, produce the oxidation interlayer defect, it is too fast to annotate ingot speed otherwise the ingot mould cooling capacity is not enough, then will produce the gravity segregation of macroscopic view in ingot casting, promptly heavier metal constituent element will be deposited on the ingot casting bottom.The ingot casting that the present invention is fit to preparation is of a size of diameter 20～50mm (garden type) or thickness of slab 15～40mm (template).
Advantage on the technology of the present invention is conspicuous: 1. it does not need complex apparatus investment and special high-temperature material, thereby the manufacturing cost of monotectic alloy is lower; 2. because the time to superheated melt pre-cooled, melt is in flow regime, it can effectively be suppressed at inevitable gravity segregation effect in the conventional static cooling procedure, has so just obtained to make the even matter monotectic alloy melt of the necessary low temperature of even matter monotectic alloy casting ingot; 3. equate with the setting rate of ingot casting owing to annotating ingot speed, so just kept a metastable little molten bath of size on ingot casting top, in this little molten bath, there is a bigger thermograde, under this thermograde drives, the forming core and the second phase drop of growing up will be done the Marangoni motion, just the opposite (because second drop such as the Pb mutually in the monotectic alloy of its direction with the gravitational field direction, the density of Bi is than parent metal height), second precipitation mutually that this effect has offset partly that gravity segregation causes in the conventional process of setting, catch at solid-liquid interface that this second static relatively phase drop will be advanced fast, thereby the present invention can obtain even matter monotectic alloy ingot casting.
Specific embodiments of the invention are described in detail in detail below.
Accompanying drawing 1 is the control casting flow process signal of monotectic alloy ball-and-roller bearing material;
Accompanying drawing 2 is the chute cut-away view;
Accompanying drawing 3 is a 10Bi90Al monotectic alloy phasor (* 12).
Embodiment 1
Preparation 10%Bi (percentage by weight, below all with), all the other are the binary monotectic alloy of Al, are 800 ℃ by the binode dotted line critical-temperature that checks in this alloy on the Al-Bi binary phase diagraml, 657 ℃ of monotectic line temperature.This alloy is put into graphite crucible, in resistance furnace, melt, and be heated to 900 ℃ (above 100 ℃ of binode dotted lines), insulation a period of time, make after its homogenising, be injected in the insulation tundish, the tundish heating-up temperature is 920 ℃.When the liquid level of alloy melt in the tundish is raised to specified altitude assignment, open the mouth of a river of tundish bottom, a special graphite spout is injected in its control carry out dynamically pre-cooledly, it is Φ 2mm that the control casting rate makes beam mouth of a river effective diameter, beam speed is 0.8m/s, (annotates ingot speed 2.5cm
3/ s), special chute and ground angle are 60 degree, and by moving air cooling, melt is after pre-cooled, and the temperature of injecting before the ingot mould is (to be higher than about about 40 ℃ of solidus temperature) about 700 ℃.Special mold is that graphite is made, internal diameter 20mm, and its ingot solidification speed is 8mm/s (2.5cm
3/ S),, promptly the unit interval amount of liquid that injects ingot mould and ingot mould in the same time amount of solidifying equate that after the cooling, obtain the uniform Al-Bi ingot casting of the second phase Bi distribution of particles, its metallographic structure as shown in Figure 3.
Embodiment 2
Preparation 10%Pb, 5%Si, all the other are the ternary monotectic alloy of Al, checking in this alloy double nodal line critical-temperature by the Al-Pb binary phase diagraml is 960 ℃, and the liquidus curve of Al-Si bianry alloy is 630 ℃, adopts as equal method as described in the embodiment 1, wherein selecting fusing and heating-up temperature for use is 1100 ℃ (being higher than 140 ℃ of binode dotted lines), the control casting rate, making beam mouth of a river effective diameter is Φ 4mm, beam speed is that 1.56m/s (annotates ingot speed 19.6cm
3/ s), the melt temperature after pre-cooled is 780 ℃ (being higher than 150 ℃ at beginning freezing point), the special chute of stainless steel, water-cooled, with the ground angle be 30 °, special mold is that stainless steel is made, water-cooled, internal diameter Φ 50mm, its ingot solidification speed 10mm/s (19.6cm
3/ s), the cooling back obtains the uniform Al-Si-Pb monotectic alloy of second phase Pb distribution of particles ingot casting.
Embodiment 3
Preparation 10%Bi, 3%Sn, 5%Si, all the other are the monotectic alloy of Al, method control casting as described in example 1 above, beam speed is 2.4m/s, mouth of a river effective diameter is that Φ 4mm (annotates ingot speed 30cm
3/ s), special mold is the stainless steel manufacturing, oil cooling, and the cast panel sectional dimension is 10 * 200mm, this alloy setting rate in mold is 15mm/s (setting rate 30cm
3/ s), obtained the uniform monotectic alloy cast panel of the second phase Bi distribution of particles after the cooling.
Embodiment 4
Preparation 20%Pb, 4%Sn, all the other are the ternary monotectic alloy of Cu, by the Cu-Pb binary phase diagraml, this alloy liquid phase line critical-temperature is 1010 ℃, and solidus (separating out Cu) is 955 ℃, with this alloy by the middle frequency furnace heat fused and be warmed up to 1200 ℃, inject 1210 ℃ insulation tundish then, the condition of control casting is: beam speed 0.6m/s, mouth of a river effective diameter Φ 5mm (annotates ingot speed 120cm
3/ s), the special chute of graphite system, assemble by three, length overall 600mm, shell is made by carbon steel, moving air cooling between shell and the graphite flake, 45 ° of chute and ground angles, melt temperature after chute is pre-cooled is 970 ℃, and special mold is a template, the cast panel sectional dimension is 40mm * 600mm, and the setting rate of this alloy in ingot mould is 5mm/s (120cm
3/ s), obtained the uniform Allen's metal cast panel of the second phase Pb distribution of particles after the cooling.
Embodiment 5
Preparation 30%Pb, 5%Sn, 1%Ni, all the other are the quaternary monotectic alloy of Cu, by the Cu-Pb binary phase diagraml, the liquidus curve critical-temperature is 990 ℃ when containing 30%Pb, 955 ℃ of solidus (separating out Cu).Adopt method as described in example 4 above, the condition of control casting is: beam speed 4.2m/s, mouth of a river effective diameter Φ 3mm (annotates ingot speed 30cm
3/ s), special mold is made by cast iron, inner water-cooled, ingot casting diameter of phi 50mm, ingot solidification speed 15mm/s (30cm
3/ s), obtained the uniform Allen's metal ingot casting of the second phase Pb distribution of particles after the cooling.
Embodiment 6
Preparation 12%Bi, 2%Sn, 10%Al, all the other are the zinc-base monotectic alloy of Zn, on the Zn-Bi binary phase diagraml, when containing Bi10%, the critical-temperature of binode dotted line is 510 ℃, 427 ℃ of monotectic line (separating out Zn) temperature, with the alloy heat fused, and after being warming up to 550 ℃, inject the insulation tundish, the control casting condition is beam speed 5.6m/s, and mouth of a river effective diameter Φ 2.1mm (annotates ingot speed 19.4cm
3/ s), carbon steel system chute, inner loop air cooling but, 440 ℃ of melt precooled temperature, the special mold internal diameter of carbon steel system 42mm, ingot solidification speed is 14mm/s (19.4cm
3/ s), obtain the uniform zinc-base monotectic alloy of second phase Bi distribution of particles ingot casting after the cooling.
The metallographic characteristics of the monotectic alloy of manufacturing of the present invention are even tissue, densification, and second particle size is moderate, Therefore good bearing performance is arranged. Take the Cu-Pb alloy as example, 30Pb, 5%Sn, all the other are the monotectic alloy of Cu for 1%Ni Adopt the bearing of the present invention's preparation, its fatigue strength is up to 60MPa, and the material of same composition is used powder metallurgic method Its fatigue strength of bearing of preparation only is 42MPa (causing the specific pressure of bearing 20% working face fatigue flake). Simultaneously, Manufacturing cost required for the present invention is also than low many of powder metallurgic method.
Claims (3)
1. the casting method of a monotectic alloy ball-and-roller bearing material is primarily aimed at following monotectic alloy:
A.Al base monotectic alloy such as Al-Bi or Al-Pb base alloy;
B.Cu base monotectic alloy such as Cu-Pb base alloy;
C.Zn base monotectic alloy such as Zn-Bi or Zn-Pb base alloy;
It is characterized in that technical process is:
(1) at first with the monotectic alloy fusing, and is heated to above 10～250 ℃ of binode dotted line, makes it become the single-phase alloy melt of uniform ingredients;
(2) ingot speed is annotated in control, the alloy melt amount of unit interval injection ingot mould is equated, i.e. v with the amount of solidifying of ingot mould alloy
1S
1=v
2S
2, v wherein
1Be the beam speed of high-temperature fusant, v
2Be setting rate in the ingot casting (being the speed of the speed that upwards pass at solid-liquid interface in the ingot mould), S
1Be water filling port net sectional area, S
2Be ingot casting sectional area, S
1/ S
2Be controlled within 0.005～0.3 scope);
(3) the monotectic alloy melt is carried out pre-cooled, make it, be generally this alloy and begin above 5～150 ℃ of freezing point near this alloy graining point;
(4) ingot casting is forced cooling, its cooling velocity should guarantee, the ingot solidification speed v
2Between 5～15mm/s, change.
2. realize the equipment of the described casting method of claim 1, comprise heating furnace (1), insulation tundish (2), ingot mould (4), it is characterized in that: the chute (3) that an available cycles water is forced cooling is set, the angle that chute (3) and ground inclination are 5 °～80 ° between tundish (2) and ingot mould (4); The outer Forced water cooling cover (5) that is added with of ingot mould (4).
3. by the described equipment of claim 2, it is characterized in that described chute (3) and ground inclination angle are at 30 °～60 °.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN94112581A CN1049168C (en) | 1994-10-26 | 1994-10-26 | Controllable casting technology for monotectic alloy antifriction bearing material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN94112581A CN1049168C (en) | 1994-10-26 | 1994-10-26 | Controllable casting technology for monotectic alloy antifriction bearing material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1121452A CN1121452A (en) | 1996-05-01 |
| CN1049168C true CN1049168C (en) | 2000-02-09 |
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|---|---|---|---|
| CN94112581A Expired - Fee Related CN1049168C (en) | 1994-10-26 | 1994-10-26 | Controllable casting technology for monotectic alloy antifriction bearing material |
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| CN100509217C (en) * | 2006-09-20 | 2009-07-08 | 中国科学院金属研究所 | Equipment for preparing monotectic alloy shell type composite tissue powder and use method thereof |
| CN107900290A (en) * | 2017-11-15 | 2018-04-13 | 贵溪博远金属有限公司 | A kind of mould for manufacturing copper pipe or copper palladium-silver bonding line |
| CN110695332A (en) * | 2019-10-17 | 2020-01-17 | 邳州市政隆建设有限公司 | Semi-automatic casting machine |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE3604861A1 (en) * | 1986-02-15 | 1987-08-20 | Battelle Development Corp | Method of producing finely dispersed alloys by powder metallurgy |
| EP0440275A1 (en) * | 1990-02-02 | 1991-08-07 | METALLGESELLSCHAFT Aktiengesellschaft | Process for making monotectic alloys |
| EP0545607A1 (en) * | 1991-11-24 | 1993-06-09 | Ontec Limited | Method and apparatus for producing homogeneous alloy |
-
1994
- 1994-10-26 CN CN94112581A patent/CN1049168C/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE3604861A1 (en) * | 1986-02-15 | 1987-08-20 | Battelle Development Corp | Method of producing finely dispersed alloys by powder metallurgy |
| EP0440275A1 (en) * | 1990-02-02 | 1991-08-07 | METALLGESELLSCHAFT Aktiengesellschaft | Process for making monotectic alloys |
| EP0545607A1 (en) * | 1991-11-24 | 1993-06-09 | Ontec Limited | Method and apparatus for producing homogeneous alloy |
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|---|---|
| CN1121452A (en) | 1996-05-01 |
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