CA2060028C - Injection part for die-casting machines - Google Patents
Injection part for die-casting machinesInfo
- Publication number
- CA2060028C CA2060028C CA002060028A CA2060028A CA2060028C CA 2060028 C CA2060028 C CA 2060028C CA 002060028 A CA002060028 A CA 002060028A CA 2060028 A CA2060028 A CA 2060028A CA 2060028 C CA2060028 C CA 2060028C
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- Prior art keywords
- powder
- alloy
- melt
- die
- examples
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
- B22D17/20—Accessories: Details
- B22D17/2015—Means for forcing the molten metal into the die
- B22D17/2023—Nozzles or shot sleeves
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
- B22D17/20—Accessories: Details
- B22D17/2015—Means for forcing the molten metal into the die
- B22D17/203—Injection pistons
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D41/00—Casting melt-holding vessels, e.g. ladles, tundishes, cups or the like
- B22D41/50—Pouring-nozzles
- B22D41/52—Manufacturing or repairing thereof
- B22D41/54—Manufacturing or repairing thereof characterised by the materials used therefor
-
- 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
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F5/007—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of moulds
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
In an injection part for die-casting machines, at least a part of a portion in contact with a melt is formed of a material which is produced by sintering a mixture of a powder of Mo or Mo alloy and the like, a powder of Ti or Ti alloy and a powder of ceramic. Here, the Mo or Mo alloy powder and the like is mixed in an amount of 0.1 to 50 % by volume. Thus obtained injection part for die-casting machine is excellent in melt-erosion resistance against melts of non-ferrous metals, impact resistance, heat retainability and wear resistance, and have a long life to thereby exhibit good work efficiency.
Description
BACKGROUND OF THE lNv~r7, ION
This invention relates to an injection part for die-casting machines, which is to be in contact with molten metal or alloy such as injection nozzles for die-casting machines. More particularly this inventionrelates to the in;ection part for die-casting machines, which is excellent in resistance to melt-erosion, impact resistance, and suitable for casting of non-ferrous metals (including alloys thereof) such as aluminum, zinc, tin and lead.
Recently, the die-casting which enables non-ferrous metals such as aluminum and the like to cast with high precision at a high speed, has become an important process of casting various kinds of parts in the fields of manufacturing automobiles, industrial equipments, household electrical appliances and the like.
Conventionally there has been used hot die steel of JIS SKD61 and the like for injection parts of die-casting machines. In recent years, there have been used injection parts for die-casting machines of such as sleeves, plungers and the like, wherein ceramic members are provided on the portion in contact with the melt by shrinkage fitting or inserting.
However, the conventional injection parts for die-casting machines stated above have problems as follows.
Firstly, in relation to the injection parts made of die steel, the portion in contact with the melt used in die-casting machines is strikingly eroded by the melt, because non-ferrous metals generally have a character tending to readily react with iron,. Consequently the injection part has only a short life, bringing about necessity for frequent exchanges thereof. Moreover steel has a high thermal conductivity, so that the temperature of the melt injected into an injection part is likely to fall down, thus markedly deteriorating production yield of casts.
On the other hand, certainly it is true that the injection parts in which a ceramic is disposed to the portion in contact with the melt, is excellent in resistance to melt-erosion, but the impact or shock exerted on the injection part at the moment when the die-casting machine injects the melt is so strong that the portion made of ceramic, which is brittle in itself, is liable to break down. If it happens, operation has to be stopped, resulting in inefficiency.
SUMMARY OF THE INVENTION
It is therefore an object of the present invention to provide an injection part for die-casting machines which is excellent in melt-erosion resistance against melts of non-ferrous metals, impact resistance, heat retainability and wear resistance, having a long life and good works efficiency.
In the injection part for die-casting machines of the present invention, at least a part of a portion in contact with melt is formed of a composite material obtained by sintering a mixture of:
a first powder of a metal or alloy selected from a group consisting of Mo, Mo alloy, Nb, Nb alloy, Ta, Ta alloys, V and V
alloys;
a second powder of Ti or a Ti alloy;
a third powder of non-oxide ceramics.
Here, the first powder of the metal or alloy such as Mo, Mo alloy or the like, is compounded in an amount of 0.1 to 50 % by volume.
The third powder is preferably compounded in an amount of 0.1 to 50 % by volume.
Since in the injection part for die-casting machines according to the present invention, at least a part of the portion in contact with the melt is formed of a composite material consisting essentially of predetermined amount of a first powder of such as Mo or Mo alloy, a second powder of such as Ti, or Ti alloy and a third powder of ceramic, it is possible to suppress erosion by melts and wear of the injection part for die-casting machines to a great extent. Moreover, since it is excellent in impact resistance to avoid cracks occurring in the part during the operation of injection, it is possible to operate the machine continuously, thus providing excellent work efficiency. The same effects VLS:lcd 2n60028 can be obtained other than Mo or Mo alloy by using Nb or Nb alloy, Ta or Ta alloy or V or V alloy.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
According to the present invention, at least a part of the portion in contact with the melt is formed of a composite material of mixture which contains predetermined amount of an Mo (molybdenum) or Mo alloy powder , a Ti (titanium) or Ti alloy powder and a ceramic powder. The composite material is prepared in such a manner that a titanium or titanium alloy powder having not only an excellent erosion resistance against melts of non-ferrous metals but also a good impact resistance, is added with ceramic particles which have high strength and hardness, further being mixed with Mo or Mo alloy particles in order to enhance the wettability between the former and the latter, so that the prepared material is made to be improved in binding performance and to be excellent in any of melt-erosion resistance, impact resistance, and wear resistance.
Moreover, the composite material is low in thermal conductivity as compared to steel, thereby exhibiting excellence in heat retainability for melts.
Accordingly, formation of this composite material into the portion in contact with melt enables the injection part for die-casting machines to have a long life excellent work efficiency.
Now, explanation will be made on reasons why each component of this composite material is to be added and why there are limitations to the compositions.
Mo Mo has an effect to better wettability between matrices consisting of metallic titanium or titanium alloy and ceramic particles to improve the binding performance therebetween, so that addition of Mo to the composite material makes improvement in impact resistance of the composite material. The Mo component can be added as Mo powder to the powder ingredients of the composite material or may be mixed as Ti-Mo alloy powder into the composite material. In the case where the Mo component is added as Ti-Mo alloy powder, three modes are possible as follows:
1. Ti-Mo alloy powder + Mo powder + ceramic powder 2. Ti-Mo alloy powder + ceramic powder 3. Ti-Mo alloy powder + Ti powder + ceramic powder In any case of 1. to 3., the Mo content in the composite material is required to be more than 0.1 % by volume on the basis of the Mo or Mo alloy powder compounded ratio. If the Mo content is less than 0.1 %
by volume, the above-stated effect of improvement in wettability cannot be obtained. This failure to improve the wettability cause the imperfection of the sintering of the material powder in production, thus deteriorating the hardness and the elongation performance. On the 6 2n60028 other hand, when the Mo content is more than 50 % by volume, the inter-metallic compound is generated between Mo and Ti in greater amount than is required, only to make the composite material brittle. Consequently the Mo content in the composite material is restricted to be 0.1 to 50 % by volume on the basis of the Mo or Mo alloy powder compounded ratio.
In place of the Mo or Mo alloy powder, the same effect is obtainable in use of Nb or Nb alloy, Ta or Ta alloy, and V or V alloy. In these cases, the content of Nb or Nb alloy, Ta or Ta alloy, or V or V alloy is restricted to the same manner.
It should be noted that there may be existing impurity component that is not removable in Mo or Mo alloy powder and in Ti or Ti alloy powder, but the present invention, needless to say, does not exclude these cases.
Ceramic Powder In a case where the content of ceramic powder in the composite material is less than 0.1% by volume, the hardness and the wear resistance of the composite material are low. On the other hand, when the content of ceramic powder in the composite material is more than 50% by volume, the composite material is made to be brittle, lowering the impact resistance to thereby be broken easily. Therefore, the content of ceramic powder in the composite material is preferably 0.1 to 50%
by volume.
The present invention will be explained in more detail showing examples of the injection parts for die-casting machines produced in practice according to the present invention with reference to their comparative examples.
In the first example, a Titanium (Ti) powder having an average particle diameter of 20 ~m and a silicon carbide (SiC) powder having an average particle diameter of 5 ~m were mixed in a ratio of 5 : 1 by volume. Then this powder mixture was added and mixed uniformly with an Mo powder having an average diameter of 15 ~ m in the proportions as shown below in Table 1.
Thus prepared mixtures were used for the starting materials.
Table.1 I I Composition (% ~y volume) ¦
¦ ¦ Ti powder + ¦ Mo powder ¦ ¦ SiC powder I ¦ M1 ¦ 99-9 ¦ 0.1 ¦ Example ¦ M2 ¦ 70 ¦ 30 ¦ ¦ M3 ¦ 50 ¦ 50 ¦ Comparative ¦ M1 ¦ 100 ¦ 0 ¦ Example ¦ M2 ¦ 48 ¦ 52 ¦ ¦ M3 ¦ 45 ¦ 55 Each of these stating materials was sealed up in a rubber-made pattern and was subjected to the cold isostatic pressing (CIP) process under the pressure of 1 ton/cm2, to form a cylinder of the pressurized powder.
Then the cylinder was sintered in a vacuum furnace at a temperature of 1,350 C a pressure of 10 5 Torr.. The sintered body was processed by the lathe to be formed into a sleeve for cold-chamber consisting of the composite material. Thus prepared sleeves were adopted as examples M1 to M3 and comparative examples M1 to M3 respectively.
Next to this, a titanium alloy powder of 45~ m in 2n60028 g average diameter comprising Mo in an amount of 15 % by volume and titanium and inevitable impurity for the rest, and tungsten carbide (WC) of 10 ~m in average diameter were mixed uniformly in the compositions as shown below in Table.2 into starting materials.
Table.2 ¦ ¦ Composition (% by volume) ¦
¦ ¦ Ti alloy ¦ WC powder ¦ ¦ powder ¦ ¦ M4 ¦ 99.9 ¦ 0.1 ¦ ¦ M5 ¦ 90 ¦ 10 I Example I M6 1 70 1 30 ¦ ¦ M7 ¦ 50 ¦ 50 ¦ Comparative ¦ M4 ¦ 100 ¦ 0 I Example I M5 ¦ 48 ¦ 52 ¦ ¦ M6 ¦ 45 ¦ 55 Each of these starting materials was, as the same manner in the examples M1 to M3 and the comparative examples M1 to M3, processed by the cold isostatic pressing, and sintered in the vacuum, and thereafter the sintered body was machined by the lathe to be formed into a cylindrical composite material. By shrinking the 2n60028 obtained composite material into the conventional sleeve (made of SKD61) for cold-chamber so as to form the inner surface, a sleeve of cold-chamber was prepared to which sleeve the composite material is disposed in the portion in contact with the melt. These sleeves were adopted as examples M4 to M7 and comparative examples M4 to M6 respectively.
The sleeve of cold chamber consisting of the hot die steel (SKD61) conventionally used was adopted as conventional example 1, and the sleeve of cold-chamber with a ceramic (silicon nitride) being shrunk thereinside was adopted as Conventional example 2.
Each sleeve for examples, comparative examples, and conventional examples was examined in its performance by the tests shown as follows.
1. Hardness test Micro-Vickers hardness of the inner surface of sleeve was measured for each specimen.
2. Tensile test The elongation of the portion of the inner surface was measured for each specimen.
3. Operational suitability test Engine covers for automobile were cast in practice with aluminum alloy (ADC12) by attaching each of the sleeves to a die-casting machine for cold-chamber (capacity, 250 tons). After 10,000 shots, the sleeve was removed and examined in the melt-erosion state thereof.
The result of this test was shown below in Table.3.
Here, the melt-erosion state is represented by "Excellent" for the case where the maximum melt-eroded loss was 0.1 mm or less, by "Good" for the case of more than 0.1 mm to 0.3 mm, and by "little bad" for the case of more than 0.3mm.
`2060~28 Table.3 I l I
¦ ¦ Micro-Vickers ¦ Elongation ¦ State of ¦ ¦ hardness(HMV) ¦ (%) ¦ melt-erosion II M1 1 400 1 12 I Excellent 1I M2 1 580 1 8 I Excellent ¦ M3 ¦ 630 ¦ 2 ¦ Excellent Example I M4 1 410 1 16 I Excellent M5 1 500 1 8 I Excellent M6 1 590 1 7 I Excellent ¦ M7 ¦ 640 ¦ 3 ¦ Excellent ¦¦ M1 ¦ 280 1 17 ¦ Little bad ¦Compara-¦ M2 ¦ 710 ¦0.6 ¦Cracks arouse ¦after 900 shots¦
¦tive ¦ M3 ¦ 780 ¦0.4 ¦Cracks arouse l l l l¦after 200 shots¦
¦example ¦ M4 ¦ 350 1 18 ¦ Little bad ¦ ¦ M5 ¦ 700 ¦ 0.9 ¦ Good M6 1 730 1 0.8 ICracks arouse ¦after 500 shots¦
¦Conven- ¦1 ¦ 600 1 1.8 ¦ Little bad ¦tional ¦2 ¦ 1700 ¦ 0.1 ¦Cracks arouse ¦example ¦ l l ¦after 200 shots¦
As is apparent from Table.3, any of sleeves in the examples M1 to M7 was excellent not only in wear resistance as having a high hardness in the inner surface, but also in impact resistance as having a large elongation. Moreover the sleeves tested in the examples M1 to M7 were little eroded by melt and had no crack caused after 10,000 shots.
On the other hand, the sleeves in comparative examples M2, M3, M6 and conventional example 2 exhibited as extremely low elongations as 0.8% or less, and were found to have cracked. All the remaining sleeves, that is, sleeves in comparative examples M1, M4, MS and conventional example 1 had melt-eroded loss of more than 0.lmm, exhibiting poor resistance to melt-erosion.
Now, explanation will be made on the production test result using Nb powder in place of Mo powder. Each specimen of Nb powder for examples N1 to N7 and comparative examples N1 to N6 was prepared in the same condition and manner as in examples M1 to M7 and comparative example M1 to M6 for Mo powder except that Nb powder was used in place of Mo powder. The examples N1 to N7 and comparative examples N1 to N6 correspond examples M1 to M7 and comparative examples M1 to M6 respectively. Compositions of examples and comparative examples are shown below in Tables.4 and 5.
Hardness test, tensile test, and operational suitability test for each examples and comparative examples was made under the same condition as in the examples and comparative examples for Mo. The result is shown below in Table.6. Here, the same conventional examples in Table.3 are shown in Table.6.
Table.4 ¦ ¦ Composition (~ by volume) ¦
¦ ¦ Ti powder + ¦ Nb powder ¦ ¦ SiC powder ¦ ¦ Nl ¦ 99.9 ¦ 0.1 I ExampleI N2 1 70 1 30 ¦ ¦ N3 ¦ 50 ¦ 50 ¦ Comparative ¦ Nl ¦ 100 ¦ 0 I Example I N2 1 48 ¦ 52 ¦ ¦ N3 ¦ 45 ¦ 55 Table.5 ¦ ¦ Composition (% by volume) ¦
¦ ¦ Ti alloy ¦ WC powder ¦ ¦ powder ¦ ¦ N4 ¦ 99.9 ¦ 0.1 ¦ ¦ N5 ¦ 90 1 10 ¦ Example ¦ N6 ¦ 70 ¦ 30 ¦ ¦ N7 ¦ 50 ¦ 50 ¦ Comparative ¦ N4 ¦ 100 ¦ 0 I Example I N5 1 48 ¦ 52 ¦ ¦ N6 ¦ 45 ¦ 55 Table.6 ¦ ¦ Micro-Vickers ¦ Elongation ¦ State of ¦ hardness(HMv) ¦ (%) ¦ melt-erosion I I N1 1 420 1 13 I Excellent 1 ¦ N2 ¦ 600 ¦ 8 ¦ Excellent I I N3 ¦ 640 1 2 I Excellent ¦Example ¦ N4 ¦430 1 15 ¦ Excellent N5 ¦ 520 1 9 I Excellent ¦ N6 ¦580 ¦ 6 ¦ Excellent ¦ N7 ¦650 ¦ 3 ¦ Excellent ¦ ¦ N1 ¦ 290 ¦ 18 ¦ Little bad ¦Compara-¦ N2 ¦ 720 ¦ 0.7 ¦Cracks arouse ¦after 800 shots¦
¦tive ¦ N3 ¦ 790 ¦ 0.4 ¦Cracks arouse ¦after 250 shots¦
¦example ¦ N4 ¦360 1 19 ¦ Little bad ¦ ¦ N5 ¦ 700 ¦ 0.9 ¦ Good ¦ ¦ N6 ¦ 720 ¦ 0.8 ¦Cracks arouse ¦after 400 shots¦
¦Conven- ¦1 ¦ 600 1 1.8 ¦ Little bad ¦tional ¦2 ¦ 1700 ¦ 0.1 ¦Cracks arouse ¦example ¦ l l ¦after 200 shots¦
As is apparent from Table.6, any of sleeves in the examples M1 to M7 was excellent not only in wear resistance as having a high hardness in the inner surface, but also in impact resistance as having a large elongation. Moreover the sleeves tested in the examples N1 to N7 were little eroded by melt and had no crack caused after 10,000 shots.
On the other hand, the sleeves in comparative examples N2, N3, N6 and conventional example 2 exhibited as extremely low elongations as 0.8~ or less, and were found to have cracked. All the remaining sleeves, that is, sleeves in comparative examples N1, N4, N5 and conventional example 1 had melt-eroded loss of more than O.lmm, exhibiting poor resistance to melt erosion.
Next, explanation will be made on the test result using Ta powder in place of Mo powder. Also in this case each specimen of Ta powder for examples Tl to T7 and comparative examples T1 to T6 was prepared in the same composition, preparing condition and testing condition as in examples for Mo powder except that Ta powder was used in place of Mo powder. Compositions of examples and comparative examples are shown below in Tables.7 and 8, and the test result is shown in Table.9.
2060o28 Table.7 ¦ ¦ Composition (% by volume) ¦
¦ ¦ Ti powder + ¦ Ta powder ¦ ¦ SiC powder ¦ ¦ T1 ¦ 99.9 ¦ 0.1 ¦ Example¦ T2 ¦ 70 1 30 ¦ ¦ T3 ¦ 50 ¦ 50 ¦ Comparative ¦ T1 ¦ 100 ¦ 0 I Example I T2 1 48 ¦ 52 ¦ ¦ T3 ¦ 45 ¦ 55 Table.8 ¦ ¦ Composition (~ by volume) ¦
¦ ¦ Ti alloy ¦ WC powder I ¦ powder ¦ ¦ T4 ¦ 99.9 ¦ 0.1 ¦ ¦ T5 ¦ 90 1 10 I ExampleI T6 1 70 1 30 ¦ ¦ T7 ¦ 50 ¦ 50 ¦ Comparative ¦ T4 ¦ 100 ¦ 0 I Example I T5 ¦ 48 ¦ 52 ¦ ¦ T6 ¦ 45 ¦ 55 -2n60028 Table.9 ¦ ¦ Micro-Vickers ¦ Elongation ¦ State of I ¦ hardness(HMv) ¦ (~) ¦ melt-erosion ¦ ¦ Tl ¦ 410 ¦ 12 ¦ Excellent 1 I T2 ¦ 630 1 6 I Excellent ¦ T3 ¦ 650 ¦ 2 ¦ Excellent ¦Example ¦ T4 ¦580 ¦ 13 ¦ Excellent I I T5 1 530 ¦ 8 I Excellent ¦ ¦ T6 ¦ 570 ¦ 6 ¦ Excellent I ¦ T7 ¦ 660 ¦ 3 ¦ Excellent ¦ ¦ Tl ¦ 290 1 16 ¦ Little bad ¦Compara-¦ T2 ¦ 750 ¦ 0.6 ¦Cracks arouse l l l l ¦after 900 shots¦
¦tive ¦ T3 ¦ 780 ¦ 0.3 ¦Cracks arouse l l l l ¦after 350 shots¦
¦example ¦ T4 ¦350 1 17 ¦ Little bad 1 I T5 ¦ 720 ¦ 0.8 ¦ Good ¦ ¦ T6 ¦ 730 ¦ 0.7 ¦Cracks arouse l l l l ¦after 450 shots¦
¦Conven- ¦1 ¦ 600 1 1.8 ¦ Little bad ¦tional ¦2 ¦ 1700 ¦ 0.1 ¦Cracks arouse ¦example ¦ l l ¦after 200 shots¦
As is apparent from Table.9, any of sleeves in the examples Tl to T7 was excellent not only in wear resistance as having a high hardness in the inner surface, but also in impact resistance as having a large elongation. Moreover the sleeves tested in the examples Tl to T7 were little eroded by melt and had no crack 19- 2~60028 caused after 10,000 shots.
On the other hand, the sleeves in comparative examples T2, T3, T6 and conventional example 2 exhibited as extremely low elongations as 0.8% or less, and were found to have cracked. All the remaining sleeves, that is, sleeves in comparative examples T1, T4, T5 and conventional example 1 had melt-eroded loss of more than 0.lmm, exhibiting poor resistance to melt-erosion.
Next, explanation will be made on the test result of examples V1 to V7 and comparative examples V1 to V6 using V powder in place of Mo powder. The compositions, production conditions and testing conditions for each specimen were the same as in the examples and comparative examples for Mo powder. Compositions of examples and comparative examples are shown below in Tables.10 and 11, and the test result is shown in Table.12.
206002~8 Table.10 ¦ ¦ Composition (% by volume) ¦
¦ ¦ Ti powder + ¦ V powder ¦ ¦ SiC powder I I V1 1 99-9 1 0.1 ¦ Example¦ V2 ¦ 70 ¦ 30 I Comparative I V1 1 100 ¦ 0 ¦ Example ¦ V2 ¦ 48 ¦ 52 Table.11 ¦ ¦ Composition (~ by volume) ¦
¦ ¦ Ti alloy ¦ WC powder ¦ ¦ powder V4 1 99.9 1 0.1 ¦ Example¦ V6 ¦ 70 ¦ 30 I Comparative I V4 1 100 1 0 ¦ Example ¦ V5 ¦ 48 ¦ 52 2~60028 Table.12 ¦ ¦ Micro-Vickers ¦ Elongation ¦ State of I ¦ hardness(HMv) ¦ (%) ¦ melt-erosion ¦ ¦ Vl ¦ 425 1 12 ¦ Excellent 1 ¦ V2 ¦ 610 ¦ 6 ¦ Excellent ¦ ¦ V3 ¦ 630 ¦ 2 ¦ Excellent ¦Example ¦ V4 ¦550 1 13 ¦ Excellent I ¦ V5 ¦ 520 ¦ 8 ¦ Excellent ¦ ¦ V6 ¦ 560 ¦ 6 ¦ Excellent ¦ ¦ V7 ¦ 650 ¦ 3 ¦ Excellent ¦ Vl 1 285 1 17 ¦ Little bad ¦Compara-¦ V2 ¦ 755 ¦ 0.6 ¦Cracks arouse l l l l ¦after 700 shots¦
¦tive ¦ V3 ¦ 770 ¦ 0.4 ¦Cracks arouse l l l l ¦after 380 shots¦
¦example ¦ V4 ¦360 1 17 ¦ Little bad ¦ ¦ V5 ¦ 730 1 0.9 ¦ Good ¦ V6 ¦740 ¦ 0.6 ¦Cracks arouse l l l l ¦after 500 shots¦
¦Conven- ¦1 ¦ 600 1 1.8 ¦ Little bad ¦tional ¦2 ¦ 1700 ¦ 0.1 ¦Cracks arouse ¦example ¦ l l ¦after 200 shots¦
As is apparent from Table.12, any of sleeves in the examples Vl to V7 was excellent not only in wear resistance as having a high hardness in the inner surface, but also in impact resistance as having a large elongation. Moreover the sleeves tested in the examples Vl to V7 were little eroded by melt and had no crack 2n60028 caused after 10,000 shots.
On the other hand, the sleeves in comparative examples V2, V3, V6 and conventional example 2 exhibited as extremely low elongations as 0.8% or less, and were found to have cracked. All the remaining sleeves, that is, sleeves in comparative examples V1, V4, V5 and conventional example 1 had melt-eroded loss of more than O.lmm, exhibiting poor resistance to melt-erosion.
It should be noted that the non-oxide ceramics applicable to the present invention are not limited to SiC and WC stated above, but various kinds of non-oxide ceramics can be used; nitride ceramics such as Si3N4, TiN, BN, AlN and the like; carbide ceramics such as TiC, B4C, CrC2 and the like; boride ceramics such as ZrBz, TiB2 and the like; and SIALON and etc. It is also possible to use more than two kinds of non-oxide ceramics in combination.
The above detailed explanation of examples are made as to sleeves for cold-chamber, but it is possible to form the composite material comprising Mo or Mo alloy powder and the like, titanium or titanium alloy powder and ceramic powder into these injection parts for die-casting machines such as plunger tip and sleeve bush for cold-chamber, and the sleeve, plunger ring, plunger tip and nozzle for hot-chamber as well as melt transport pipe and the like.
VLS:lcd
This invention relates to an injection part for die-casting machines, which is to be in contact with molten metal or alloy such as injection nozzles for die-casting machines. More particularly this inventionrelates to the in;ection part for die-casting machines, which is excellent in resistance to melt-erosion, impact resistance, and suitable for casting of non-ferrous metals (including alloys thereof) such as aluminum, zinc, tin and lead.
Recently, the die-casting which enables non-ferrous metals such as aluminum and the like to cast with high precision at a high speed, has become an important process of casting various kinds of parts in the fields of manufacturing automobiles, industrial equipments, household electrical appliances and the like.
Conventionally there has been used hot die steel of JIS SKD61 and the like for injection parts of die-casting machines. In recent years, there have been used injection parts for die-casting machines of such as sleeves, plungers and the like, wherein ceramic members are provided on the portion in contact with the melt by shrinkage fitting or inserting.
However, the conventional injection parts for die-casting machines stated above have problems as follows.
Firstly, in relation to the injection parts made of die steel, the portion in contact with the melt used in die-casting machines is strikingly eroded by the melt, because non-ferrous metals generally have a character tending to readily react with iron,. Consequently the injection part has only a short life, bringing about necessity for frequent exchanges thereof. Moreover steel has a high thermal conductivity, so that the temperature of the melt injected into an injection part is likely to fall down, thus markedly deteriorating production yield of casts.
On the other hand, certainly it is true that the injection parts in which a ceramic is disposed to the portion in contact with the melt, is excellent in resistance to melt-erosion, but the impact or shock exerted on the injection part at the moment when the die-casting machine injects the melt is so strong that the portion made of ceramic, which is brittle in itself, is liable to break down. If it happens, operation has to be stopped, resulting in inefficiency.
SUMMARY OF THE INVENTION
It is therefore an object of the present invention to provide an injection part for die-casting machines which is excellent in melt-erosion resistance against melts of non-ferrous metals, impact resistance, heat retainability and wear resistance, having a long life and good works efficiency.
In the injection part for die-casting machines of the present invention, at least a part of a portion in contact with melt is formed of a composite material obtained by sintering a mixture of:
a first powder of a metal or alloy selected from a group consisting of Mo, Mo alloy, Nb, Nb alloy, Ta, Ta alloys, V and V
alloys;
a second powder of Ti or a Ti alloy;
a third powder of non-oxide ceramics.
Here, the first powder of the metal or alloy such as Mo, Mo alloy or the like, is compounded in an amount of 0.1 to 50 % by volume.
The third powder is preferably compounded in an amount of 0.1 to 50 % by volume.
Since in the injection part for die-casting machines according to the present invention, at least a part of the portion in contact with the melt is formed of a composite material consisting essentially of predetermined amount of a first powder of such as Mo or Mo alloy, a second powder of such as Ti, or Ti alloy and a third powder of ceramic, it is possible to suppress erosion by melts and wear of the injection part for die-casting machines to a great extent. Moreover, since it is excellent in impact resistance to avoid cracks occurring in the part during the operation of injection, it is possible to operate the machine continuously, thus providing excellent work efficiency. The same effects VLS:lcd 2n60028 can be obtained other than Mo or Mo alloy by using Nb or Nb alloy, Ta or Ta alloy or V or V alloy.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
According to the present invention, at least a part of the portion in contact with the melt is formed of a composite material of mixture which contains predetermined amount of an Mo (molybdenum) or Mo alloy powder , a Ti (titanium) or Ti alloy powder and a ceramic powder. The composite material is prepared in such a manner that a titanium or titanium alloy powder having not only an excellent erosion resistance against melts of non-ferrous metals but also a good impact resistance, is added with ceramic particles which have high strength and hardness, further being mixed with Mo or Mo alloy particles in order to enhance the wettability between the former and the latter, so that the prepared material is made to be improved in binding performance and to be excellent in any of melt-erosion resistance, impact resistance, and wear resistance.
Moreover, the composite material is low in thermal conductivity as compared to steel, thereby exhibiting excellence in heat retainability for melts.
Accordingly, formation of this composite material into the portion in contact with melt enables the injection part for die-casting machines to have a long life excellent work efficiency.
Now, explanation will be made on reasons why each component of this composite material is to be added and why there are limitations to the compositions.
Mo Mo has an effect to better wettability between matrices consisting of metallic titanium or titanium alloy and ceramic particles to improve the binding performance therebetween, so that addition of Mo to the composite material makes improvement in impact resistance of the composite material. The Mo component can be added as Mo powder to the powder ingredients of the composite material or may be mixed as Ti-Mo alloy powder into the composite material. In the case where the Mo component is added as Ti-Mo alloy powder, three modes are possible as follows:
1. Ti-Mo alloy powder + Mo powder + ceramic powder 2. Ti-Mo alloy powder + ceramic powder 3. Ti-Mo alloy powder + Ti powder + ceramic powder In any case of 1. to 3., the Mo content in the composite material is required to be more than 0.1 % by volume on the basis of the Mo or Mo alloy powder compounded ratio. If the Mo content is less than 0.1 %
by volume, the above-stated effect of improvement in wettability cannot be obtained. This failure to improve the wettability cause the imperfection of the sintering of the material powder in production, thus deteriorating the hardness and the elongation performance. On the 6 2n60028 other hand, when the Mo content is more than 50 % by volume, the inter-metallic compound is generated between Mo and Ti in greater amount than is required, only to make the composite material brittle. Consequently the Mo content in the composite material is restricted to be 0.1 to 50 % by volume on the basis of the Mo or Mo alloy powder compounded ratio.
In place of the Mo or Mo alloy powder, the same effect is obtainable in use of Nb or Nb alloy, Ta or Ta alloy, and V or V alloy. In these cases, the content of Nb or Nb alloy, Ta or Ta alloy, or V or V alloy is restricted to the same manner.
It should be noted that there may be existing impurity component that is not removable in Mo or Mo alloy powder and in Ti or Ti alloy powder, but the present invention, needless to say, does not exclude these cases.
Ceramic Powder In a case where the content of ceramic powder in the composite material is less than 0.1% by volume, the hardness and the wear resistance of the composite material are low. On the other hand, when the content of ceramic powder in the composite material is more than 50% by volume, the composite material is made to be brittle, lowering the impact resistance to thereby be broken easily. Therefore, the content of ceramic powder in the composite material is preferably 0.1 to 50%
by volume.
The present invention will be explained in more detail showing examples of the injection parts for die-casting machines produced in practice according to the present invention with reference to their comparative examples.
In the first example, a Titanium (Ti) powder having an average particle diameter of 20 ~m and a silicon carbide (SiC) powder having an average particle diameter of 5 ~m were mixed in a ratio of 5 : 1 by volume. Then this powder mixture was added and mixed uniformly with an Mo powder having an average diameter of 15 ~ m in the proportions as shown below in Table 1.
Thus prepared mixtures were used for the starting materials.
Table.1 I I Composition (% ~y volume) ¦
¦ ¦ Ti powder + ¦ Mo powder ¦ ¦ SiC powder I ¦ M1 ¦ 99-9 ¦ 0.1 ¦ Example ¦ M2 ¦ 70 ¦ 30 ¦ ¦ M3 ¦ 50 ¦ 50 ¦ Comparative ¦ M1 ¦ 100 ¦ 0 ¦ Example ¦ M2 ¦ 48 ¦ 52 ¦ ¦ M3 ¦ 45 ¦ 55 Each of these stating materials was sealed up in a rubber-made pattern and was subjected to the cold isostatic pressing (CIP) process under the pressure of 1 ton/cm2, to form a cylinder of the pressurized powder.
Then the cylinder was sintered in a vacuum furnace at a temperature of 1,350 C a pressure of 10 5 Torr.. The sintered body was processed by the lathe to be formed into a sleeve for cold-chamber consisting of the composite material. Thus prepared sleeves were adopted as examples M1 to M3 and comparative examples M1 to M3 respectively.
Next to this, a titanium alloy powder of 45~ m in 2n60028 g average diameter comprising Mo in an amount of 15 % by volume and titanium and inevitable impurity for the rest, and tungsten carbide (WC) of 10 ~m in average diameter were mixed uniformly in the compositions as shown below in Table.2 into starting materials.
Table.2 ¦ ¦ Composition (% by volume) ¦
¦ ¦ Ti alloy ¦ WC powder ¦ ¦ powder ¦ ¦ M4 ¦ 99.9 ¦ 0.1 ¦ ¦ M5 ¦ 90 ¦ 10 I Example I M6 1 70 1 30 ¦ ¦ M7 ¦ 50 ¦ 50 ¦ Comparative ¦ M4 ¦ 100 ¦ 0 I Example I M5 ¦ 48 ¦ 52 ¦ ¦ M6 ¦ 45 ¦ 55 Each of these starting materials was, as the same manner in the examples M1 to M3 and the comparative examples M1 to M3, processed by the cold isostatic pressing, and sintered in the vacuum, and thereafter the sintered body was machined by the lathe to be formed into a cylindrical composite material. By shrinking the 2n60028 obtained composite material into the conventional sleeve (made of SKD61) for cold-chamber so as to form the inner surface, a sleeve of cold-chamber was prepared to which sleeve the composite material is disposed in the portion in contact with the melt. These sleeves were adopted as examples M4 to M7 and comparative examples M4 to M6 respectively.
The sleeve of cold chamber consisting of the hot die steel (SKD61) conventionally used was adopted as conventional example 1, and the sleeve of cold-chamber with a ceramic (silicon nitride) being shrunk thereinside was adopted as Conventional example 2.
Each sleeve for examples, comparative examples, and conventional examples was examined in its performance by the tests shown as follows.
1. Hardness test Micro-Vickers hardness of the inner surface of sleeve was measured for each specimen.
2. Tensile test The elongation of the portion of the inner surface was measured for each specimen.
3. Operational suitability test Engine covers for automobile were cast in practice with aluminum alloy (ADC12) by attaching each of the sleeves to a die-casting machine for cold-chamber (capacity, 250 tons). After 10,000 shots, the sleeve was removed and examined in the melt-erosion state thereof.
The result of this test was shown below in Table.3.
Here, the melt-erosion state is represented by "Excellent" for the case where the maximum melt-eroded loss was 0.1 mm or less, by "Good" for the case of more than 0.1 mm to 0.3 mm, and by "little bad" for the case of more than 0.3mm.
`2060~28 Table.3 I l I
¦ ¦ Micro-Vickers ¦ Elongation ¦ State of ¦ ¦ hardness(HMV) ¦ (%) ¦ melt-erosion II M1 1 400 1 12 I Excellent 1I M2 1 580 1 8 I Excellent ¦ M3 ¦ 630 ¦ 2 ¦ Excellent Example I M4 1 410 1 16 I Excellent M5 1 500 1 8 I Excellent M6 1 590 1 7 I Excellent ¦ M7 ¦ 640 ¦ 3 ¦ Excellent ¦¦ M1 ¦ 280 1 17 ¦ Little bad ¦Compara-¦ M2 ¦ 710 ¦0.6 ¦Cracks arouse ¦after 900 shots¦
¦tive ¦ M3 ¦ 780 ¦0.4 ¦Cracks arouse l l l l¦after 200 shots¦
¦example ¦ M4 ¦ 350 1 18 ¦ Little bad ¦ ¦ M5 ¦ 700 ¦ 0.9 ¦ Good M6 1 730 1 0.8 ICracks arouse ¦after 500 shots¦
¦Conven- ¦1 ¦ 600 1 1.8 ¦ Little bad ¦tional ¦2 ¦ 1700 ¦ 0.1 ¦Cracks arouse ¦example ¦ l l ¦after 200 shots¦
As is apparent from Table.3, any of sleeves in the examples M1 to M7 was excellent not only in wear resistance as having a high hardness in the inner surface, but also in impact resistance as having a large elongation. Moreover the sleeves tested in the examples M1 to M7 were little eroded by melt and had no crack caused after 10,000 shots.
On the other hand, the sleeves in comparative examples M2, M3, M6 and conventional example 2 exhibited as extremely low elongations as 0.8% or less, and were found to have cracked. All the remaining sleeves, that is, sleeves in comparative examples M1, M4, MS and conventional example 1 had melt-eroded loss of more than 0.lmm, exhibiting poor resistance to melt-erosion.
Now, explanation will be made on the production test result using Nb powder in place of Mo powder. Each specimen of Nb powder for examples N1 to N7 and comparative examples N1 to N6 was prepared in the same condition and manner as in examples M1 to M7 and comparative example M1 to M6 for Mo powder except that Nb powder was used in place of Mo powder. The examples N1 to N7 and comparative examples N1 to N6 correspond examples M1 to M7 and comparative examples M1 to M6 respectively. Compositions of examples and comparative examples are shown below in Tables.4 and 5.
Hardness test, tensile test, and operational suitability test for each examples and comparative examples was made under the same condition as in the examples and comparative examples for Mo. The result is shown below in Table.6. Here, the same conventional examples in Table.3 are shown in Table.6.
Table.4 ¦ ¦ Composition (~ by volume) ¦
¦ ¦ Ti powder + ¦ Nb powder ¦ ¦ SiC powder ¦ ¦ Nl ¦ 99.9 ¦ 0.1 I ExampleI N2 1 70 1 30 ¦ ¦ N3 ¦ 50 ¦ 50 ¦ Comparative ¦ Nl ¦ 100 ¦ 0 I Example I N2 1 48 ¦ 52 ¦ ¦ N3 ¦ 45 ¦ 55 Table.5 ¦ ¦ Composition (% by volume) ¦
¦ ¦ Ti alloy ¦ WC powder ¦ ¦ powder ¦ ¦ N4 ¦ 99.9 ¦ 0.1 ¦ ¦ N5 ¦ 90 1 10 ¦ Example ¦ N6 ¦ 70 ¦ 30 ¦ ¦ N7 ¦ 50 ¦ 50 ¦ Comparative ¦ N4 ¦ 100 ¦ 0 I Example I N5 1 48 ¦ 52 ¦ ¦ N6 ¦ 45 ¦ 55 Table.6 ¦ ¦ Micro-Vickers ¦ Elongation ¦ State of ¦ hardness(HMv) ¦ (%) ¦ melt-erosion I I N1 1 420 1 13 I Excellent 1 ¦ N2 ¦ 600 ¦ 8 ¦ Excellent I I N3 ¦ 640 1 2 I Excellent ¦Example ¦ N4 ¦430 1 15 ¦ Excellent N5 ¦ 520 1 9 I Excellent ¦ N6 ¦580 ¦ 6 ¦ Excellent ¦ N7 ¦650 ¦ 3 ¦ Excellent ¦ ¦ N1 ¦ 290 ¦ 18 ¦ Little bad ¦Compara-¦ N2 ¦ 720 ¦ 0.7 ¦Cracks arouse ¦after 800 shots¦
¦tive ¦ N3 ¦ 790 ¦ 0.4 ¦Cracks arouse ¦after 250 shots¦
¦example ¦ N4 ¦360 1 19 ¦ Little bad ¦ ¦ N5 ¦ 700 ¦ 0.9 ¦ Good ¦ ¦ N6 ¦ 720 ¦ 0.8 ¦Cracks arouse ¦after 400 shots¦
¦Conven- ¦1 ¦ 600 1 1.8 ¦ Little bad ¦tional ¦2 ¦ 1700 ¦ 0.1 ¦Cracks arouse ¦example ¦ l l ¦after 200 shots¦
As is apparent from Table.6, any of sleeves in the examples M1 to M7 was excellent not only in wear resistance as having a high hardness in the inner surface, but also in impact resistance as having a large elongation. Moreover the sleeves tested in the examples N1 to N7 were little eroded by melt and had no crack caused after 10,000 shots.
On the other hand, the sleeves in comparative examples N2, N3, N6 and conventional example 2 exhibited as extremely low elongations as 0.8~ or less, and were found to have cracked. All the remaining sleeves, that is, sleeves in comparative examples N1, N4, N5 and conventional example 1 had melt-eroded loss of more than O.lmm, exhibiting poor resistance to melt erosion.
Next, explanation will be made on the test result using Ta powder in place of Mo powder. Also in this case each specimen of Ta powder for examples Tl to T7 and comparative examples T1 to T6 was prepared in the same composition, preparing condition and testing condition as in examples for Mo powder except that Ta powder was used in place of Mo powder. Compositions of examples and comparative examples are shown below in Tables.7 and 8, and the test result is shown in Table.9.
2060o28 Table.7 ¦ ¦ Composition (% by volume) ¦
¦ ¦ Ti powder + ¦ Ta powder ¦ ¦ SiC powder ¦ ¦ T1 ¦ 99.9 ¦ 0.1 ¦ Example¦ T2 ¦ 70 1 30 ¦ ¦ T3 ¦ 50 ¦ 50 ¦ Comparative ¦ T1 ¦ 100 ¦ 0 I Example I T2 1 48 ¦ 52 ¦ ¦ T3 ¦ 45 ¦ 55 Table.8 ¦ ¦ Composition (~ by volume) ¦
¦ ¦ Ti alloy ¦ WC powder I ¦ powder ¦ ¦ T4 ¦ 99.9 ¦ 0.1 ¦ ¦ T5 ¦ 90 1 10 I ExampleI T6 1 70 1 30 ¦ ¦ T7 ¦ 50 ¦ 50 ¦ Comparative ¦ T4 ¦ 100 ¦ 0 I Example I T5 ¦ 48 ¦ 52 ¦ ¦ T6 ¦ 45 ¦ 55 -2n60028 Table.9 ¦ ¦ Micro-Vickers ¦ Elongation ¦ State of I ¦ hardness(HMv) ¦ (~) ¦ melt-erosion ¦ ¦ Tl ¦ 410 ¦ 12 ¦ Excellent 1 I T2 ¦ 630 1 6 I Excellent ¦ T3 ¦ 650 ¦ 2 ¦ Excellent ¦Example ¦ T4 ¦580 ¦ 13 ¦ Excellent I I T5 1 530 ¦ 8 I Excellent ¦ ¦ T6 ¦ 570 ¦ 6 ¦ Excellent I ¦ T7 ¦ 660 ¦ 3 ¦ Excellent ¦ ¦ Tl ¦ 290 1 16 ¦ Little bad ¦Compara-¦ T2 ¦ 750 ¦ 0.6 ¦Cracks arouse l l l l ¦after 900 shots¦
¦tive ¦ T3 ¦ 780 ¦ 0.3 ¦Cracks arouse l l l l ¦after 350 shots¦
¦example ¦ T4 ¦350 1 17 ¦ Little bad 1 I T5 ¦ 720 ¦ 0.8 ¦ Good ¦ ¦ T6 ¦ 730 ¦ 0.7 ¦Cracks arouse l l l l ¦after 450 shots¦
¦Conven- ¦1 ¦ 600 1 1.8 ¦ Little bad ¦tional ¦2 ¦ 1700 ¦ 0.1 ¦Cracks arouse ¦example ¦ l l ¦after 200 shots¦
As is apparent from Table.9, any of sleeves in the examples Tl to T7 was excellent not only in wear resistance as having a high hardness in the inner surface, but also in impact resistance as having a large elongation. Moreover the sleeves tested in the examples Tl to T7 were little eroded by melt and had no crack 19- 2~60028 caused after 10,000 shots.
On the other hand, the sleeves in comparative examples T2, T3, T6 and conventional example 2 exhibited as extremely low elongations as 0.8% or less, and were found to have cracked. All the remaining sleeves, that is, sleeves in comparative examples T1, T4, T5 and conventional example 1 had melt-eroded loss of more than 0.lmm, exhibiting poor resistance to melt-erosion.
Next, explanation will be made on the test result of examples V1 to V7 and comparative examples V1 to V6 using V powder in place of Mo powder. The compositions, production conditions and testing conditions for each specimen were the same as in the examples and comparative examples for Mo powder. Compositions of examples and comparative examples are shown below in Tables.10 and 11, and the test result is shown in Table.12.
206002~8 Table.10 ¦ ¦ Composition (% by volume) ¦
¦ ¦ Ti powder + ¦ V powder ¦ ¦ SiC powder I I V1 1 99-9 1 0.1 ¦ Example¦ V2 ¦ 70 ¦ 30 I Comparative I V1 1 100 ¦ 0 ¦ Example ¦ V2 ¦ 48 ¦ 52 Table.11 ¦ ¦ Composition (~ by volume) ¦
¦ ¦ Ti alloy ¦ WC powder ¦ ¦ powder V4 1 99.9 1 0.1 ¦ Example¦ V6 ¦ 70 ¦ 30 I Comparative I V4 1 100 1 0 ¦ Example ¦ V5 ¦ 48 ¦ 52 2~60028 Table.12 ¦ ¦ Micro-Vickers ¦ Elongation ¦ State of I ¦ hardness(HMv) ¦ (%) ¦ melt-erosion ¦ ¦ Vl ¦ 425 1 12 ¦ Excellent 1 ¦ V2 ¦ 610 ¦ 6 ¦ Excellent ¦ ¦ V3 ¦ 630 ¦ 2 ¦ Excellent ¦Example ¦ V4 ¦550 1 13 ¦ Excellent I ¦ V5 ¦ 520 ¦ 8 ¦ Excellent ¦ ¦ V6 ¦ 560 ¦ 6 ¦ Excellent ¦ ¦ V7 ¦ 650 ¦ 3 ¦ Excellent ¦ Vl 1 285 1 17 ¦ Little bad ¦Compara-¦ V2 ¦ 755 ¦ 0.6 ¦Cracks arouse l l l l ¦after 700 shots¦
¦tive ¦ V3 ¦ 770 ¦ 0.4 ¦Cracks arouse l l l l ¦after 380 shots¦
¦example ¦ V4 ¦360 1 17 ¦ Little bad ¦ ¦ V5 ¦ 730 1 0.9 ¦ Good ¦ V6 ¦740 ¦ 0.6 ¦Cracks arouse l l l l ¦after 500 shots¦
¦Conven- ¦1 ¦ 600 1 1.8 ¦ Little bad ¦tional ¦2 ¦ 1700 ¦ 0.1 ¦Cracks arouse ¦example ¦ l l ¦after 200 shots¦
As is apparent from Table.12, any of sleeves in the examples Vl to V7 was excellent not only in wear resistance as having a high hardness in the inner surface, but also in impact resistance as having a large elongation. Moreover the sleeves tested in the examples Vl to V7 were little eroded by melt and had no crack 2n60028 caused after 10,000 shots.
On the other hand, the sleeves in comparative examples V2, V3, V6 and conventional example 2 exhibited as extremely low elongations as 0.8% or less, and were found to have cracked. All the remaining sleeves, that is, sleeves in comparative examples V1, V4, V5 and conventional example 1 had melt-eroded loss of more than O.lmm, exhibiting poor resistance to melt-erosion.
It should be noted that the non-oxide ceramics applicable to the present invention are not limited to SiC and WC stated above, but various kinds of non-oxide ceramics can be used; nitride ceramics such as Si3N4, TiN, BN, AlN and the like; carbide ceramics such as TiC, B4C, CrC2 and the like; boride ceramics such as ZrBz, TiB2 and the like; and SIALON and etc. It is also possible to use more than two kinds of non-oxide ceramics in combination.
The above detailed explanation of examples are made as to sleeves for cold-chamber, but it is possible to form the composite material comprising Mo or Mo alloy powder and the like, titanium or titanium alloy powder and ceramic powder into these injection parts for die-casting machines such as plunger tip and sleeve bush for cold-chamber, and the sleeve, plunger ring, plunger tip and nozzle for hot-chamber as well as melt transport pipe and the like.
VLS:lcd
Claims (3)
1. An injection part for die-casting machines characterized in that at least a part of a portion which is to be in contact with melt is formed of a composite material obtained by sintering a mixture of:
a first powder of a metal or alloy selected from a group consisting of Mo, Mo alloy, Nb, Nb alloy, Ta, Ta alloy, V and V
alloy:
a second powder of Ti or Ti alloy;
a third powder of non-oxide ceramics, wherein said first powder is compounded in an amount of 0.1 to 50 %
by volume based on the total amount of said mixture.
a first powder of a metal or alloy selected from a group consisting of Mo, Mo alloy, Nb, Nb alloy, Ta, Ta alloy, V and V
alloy:
a second powder of Ti or Ti alloy;
a third powder of non-oxide ceramics, wherein said first powder is compounded in an amount of 0.1 to 50 %
by volume based on the total amount of said mixture.
2. An injection part according to claim 1, wherein said third powder is compounded in an amount of 0.1 to 50 % by volume based on the total amount of said mixture.
3. An injection part according to claim 1, wherein said non-oxide ceramics is a ceramic or a mixture of ceramics selected from the group consisting of SiC, WC, Si3N4, TiN, BN, AlN, TiC, B4C, CrC2, ZrB2, TiB2 and SIALON.
Applications Claiming Priority (8)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3-25409 | 1991-01-24 | ||
| JP3025410A JPH04247805A (en) | 1991-01-24 | 1991-01-24 | Injecting parts for die casting machine |
| JP3-25408 | 1991-01-24 | ||
| JP3025411A JPH04247806A (en) | 1991-01-24 | 1991-01-24 | Injecting parts for die casting machine |
| JP3-25410 | 1991-01-24 | ||
| JP3-25411 | 1991-01-24 | ||
| JP3025409A JPH04247801A (en) | 1991-01-24 | 1991-01-24 | Injecting parts for die casting machine |
| JP3025408A JPH0784601B2 (en) | 1991-01-24 | 1991-01-24 | Injection parts for die casting machine |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2060028A1 CA2060028A1 (en) | 1992-07-25 |
| CA2060028C true CA2060028C (en) | 1997-07-01 |
Family
ID=27458306
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002060028A Expired - Fee Related CA2060028C (en) | 1991-01-24 | 1992-01-24 | Injection part for die-casting machines |
Country Status (5)
| Country | Link |
|---|---|
| KR (1) | KR960006046B1 (en) |
| CA (1) | CA2060028C (en) |
| DE (1) | DE4201781C2 (en) |
| FR (1) | FR2672056B1 (en) |
| GB (1) | GB2253213B (en) |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2269182B (en) * | 1992-06-08 | 1996-09-04 | Nippon Tungsten | Titanium-base hard sintered alloy |
| US5660859A (en) * | 1994-12-29 | 1997-08-26 | Mcneil-Ppc, Inc. | Gelling agent for polyethylene glycol |
| US5711366A (en) * | 1996-05-31 | 1998-01-27 | Thixomat, Inc. | Apparatus for processing corrosive molten metals |
| DE10313089B3 (en) * | 2003-03-24 | 2004-08-19 | Drm Druckguss Gmbh | Die casting machine has a heated chamber, for the supply of molten metal, and a press unit within the chamber to take a defined volume on an axial movement and press the metal through a guide into the mold without cooling |
| DE102004061948A1 (en) * | 2004-12-22 | 2006-07-27 | Münstermann, Simon | Tool for forming high melting metal materials in thixotropic state used in e.g. thioforging of e.g. aluminum alloy, has inner layer of e.g. corrosion-resistant ceramic or metal/ceramic material and outer ceramic layer |
| DE102015016756A1 (en) * | 2015-12-23 | 2017-06-29 | Wieland-Werke Ag | Filling chamber for a die casting machine |
| EP3309266A1 (en) * | 2016-10-13 | 2018-04-18 | MTU Aero Engines GmbH | Method of making a molybdenum alloy having a high titanium content |
| CN113416875A (en) * | 2021-06-21 | 2021-09-21 | 广东欧派斯润滑科技有限公司 | High-temperature oxidation-resistant wear-resistant molybdenum alloy |
Family Cites Families (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1238376B (en) * | 1964-01-29 | 1967-04-06 | Rosenthal Ag | Ceramic materials resistant to temperature changes |
| AT245742B (en) * | 1964-12-10 | 1966-03-10 | Plansee Metallwerk | Permanent mold for casting metallic melts |
| US3441391A (en) * | 1967-01-26 | 1969-04-29 | Gen Electric | Tungsten-base alloys |
| US3486552A (en) * | 1967-06-16 | 1969-12-30 | Acme Precision Products Inc | Nozzle for injection molding |
| US3713788A (en) * | 1970-10-21 | 1973-01-30 | Chromalloy American Corp | Powder metallurgy sintered corrosion and heat-resistant, age hardenable nickel-chromium refractory carbide alloy |
| US3786552A (en) * | 1971-06-30 | 1974-01-22 | Mitsubishi Metal Mining Co Ltd | Method of manufacturing a composite bimetallic sleeve for a die-casting machine |
| DE2244470C3 (en) * | 1972-09-11 | 1975-03-13 | Deutsche Edelstahlwerke Ag, 4150 Krefeld | Highly corrosion-resistant and wear-resistant sintered steel alloy |
| DE2364809B2 (en) * | 1972-12-28 | 1978-11-30 | Denki Kagaku Kogyo K.K. | Material mixture for the cylinder and piston of an injection pump for hot chamber or cold chamber die casting machines |
| FR2308692A1 (en) * | 1975-04-23 | 1976-11-19 | Cime Bocuze | NEW PROCESS FOR PREPARATION BY SINTING OF MOLYBDENE-BASED ALLOYS WITH SOLID REINFORCING ELEMENTS |
| JPS58193335A (en) * | 1982-05-06 | 1983-11-11 | Sumitomo Electric Ind Ltd | Dispersion-strengthened nickel-based heat-resistant sintered alloy and its manufacturing method |
| JPS6036642A (en) * | 1983-08-08 | 1985-02-25 | Mitsubishi Metal Corp | Cermet for die casting mold parts |
| JPH07112623B2 (en) * | 1988-04-30 | 1995-12-06 | 東芝セラミックス株式会社 | Low melting point molten metal processing tool |
-
1992
- 1992-01-23 GB GB9201411A patent/GB2253213B/en not_active Expired - Fee Related
- 1992-01-23 KR KR1019920000912A patent/KR960006046B1/en not_active Expired - Fee Related
- 1992-01-23 DE DE4201781A patent/DE4201781C2/en not_active Expired - Fee Related
- 1992-01-24 FR FR9200789A patent/FR2672056B1/en not_active Expired - Fee Related
- 1992-01-24 CA CA002060028A patent/CA2060028C/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| KR920014946A (en) | 1992-08-26 |
| DE4201781C2 (en) | 1996-05-30 |
| GB2253213B (en) | 1995-03-08 |
| GB9201411D0 (en) | 1992-03-11 |
| KR960006046B1 (en) | 1996-05-08 |
| GB2253213A (en) | 1992-09-02 |
| DE4201781A1 (en) | 1992-07-30 |
| FR2672056A1 (en) | 1992-07-31 |
| FR2672056B1 (en) | 1994-07-22 |
| CA2060028A1 (en) | 1992-07-25 |
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