CN102317486A

CN102317486A - Magnesium based alloy

Info

Publication number: CN102317486A
Application number: CN2008801243855A
Authority: CN
Inventors: 马克·吉布森; 马克·伊斯顿; 科琳·贝特尔斯
Original assignee: Cast CRC Ltd
Current assignee: Cast CRC Ltd
Priority date: 2008-01-09
Filing date: 2008-12-23
Publication date: 2012-01-11
Also published as: US20100310409A1; EP2231890A4; EP2231890A1; AU2008346713A1; CA2711753A1; JP2011509350A; WO2009086585A1

Abstract

A magnesium based alloy consisting of, by weight: 2-5% rare earth elements, wherein the alloy contains lanthanum and cerium as rare earth elements and the lanthanum content is greater than the cerium content; 0.2-0.8% zinc; 0-0.15% aluminium; 0-0.5% yttrium or gadolinium; 0-0.2% zirconium; ' 0-0.3% manganese; 0-0.1% calcium; 0-25 ppm beryllium; and the remainder being magnesium except for incidental impurities.

Description

Magnuminium

Technical field

The present invention relates to Magnuminium, relate in particular to the Magnuminium of a kind of ability through Hpdc (HPDC) casting.

Background technology

Along with restriction fuel oil consumption and the growth of requirement of minimizing towards the noxious emission of environment, the automaker is just seeking to research and develop more fuel-efficient vehicle.The gross weight that reduces vehicle is to realize the key of this target.Arbitrarily the weight of vehicle is mainly from the miscellaneous part of mover and transmission system.The most important parts of mover are the cylinder bodys that accounts for the 20-25% of mover gross weight.Past is to replace traditional gray iron cylinder body to save most weight through introducing aluminum alloy cylinder body, if use the magnesiumalloy that can bear the temperature and pressure that produces during the running of an engine can further reduce by about 40% weight.Before considering to make feasible magnesium power pack, the development that has the alloy of required high-temperature machinery characteristic and cost-effective ME concurrently is necessary.

HPDC is a kind of technology that can be used for making on a large scale the high production capacity of light alloy components.Though the casting compactness of sand mold casting and low pressure/gravity metal mold casting is usually above HPDC, HPDC is the lower technology of cost for the scale operation of big volume.HPDC is very universal in the automaker of North America, and Europe and the Asia be the main technique that is used for the y alloy y power pack.In recent years, the high temperature Mg Alloy mainly concentrates in the HPDC technical process, and has developed several alloys.HPDC is considered to realize high efficiency and the good selection that reduces manufacturing cost.

WO2006/105594 has proposed a kind of Magnuminium, is made up of following weight part:

The 1.5-4.0% REE,

0.3-0.8% zinc,

0.02-0.1% aluminium,

The 4-25ppm beryllium,

The 0-0.2% zirconium,

0-0.3% manganese,

The 0-0.5% yttrium,

0-0.1% calcium, and

Surplus is magnesium except incidental impurity.

Be proved to be according to the alloy of WO2006/105594 and had excellent high temperature creep characteristic, but verifiedly be difficult to carry out die casting.The inventor finds, can improve flowability and the oxidation-resistance of hot tearing resistance and molten alloy during the die casting according to WO2006/105594 through the ratio that increases lanthanum in the alloy.

This specification sheets in full in, word " rare earth " is interpreted as referring to ordination number 57-71, be any or its combination in lanthanum (La) to the element of lutetium (Lu).

Summary of the invention

In first aspect, the invention provides a kind of Magnuminium, be grouped into by the one-tenth of following weight part:

The 2-5% REE, wherein this alloy comprises lanthanum and the cerium as REE, and the content of lanthanum is greater than the content of cerium;

0.2-0.8% zinc;

0.02-0.15% aluminium;

0-0.5% yttrium or gadolinium;

The 0-0.2% zirconium;

0-0.3% manganese;

0-0.1% calcium;

The 0-25ppm beryllium; And

Surplus is magnesium except incidental impurity.

The total content of lanthanum and cerium is preferably 1.5-3.5% by weight in the alloy, more preferably 1.8-3.0%, especially preferably 2.0-2.8%.Be not wishing to be bound by theory, lanthanum and cerium can improve the castibility and the strength of alloy.Moreover, being not wishing to be bound by theory, lanthanum content also can improve the hot tearing resistance of castibility, the especially alloy of alloy greater than cerium content.The ratio of lanthanum and cerium is high more can give big more ductility of alloy and big more hot tearing resistance usually.Usually, the total content of bigger lanthanum and cerium helps the creep resistance of alloy and will the reducing of the ductility of the alloy that accompanies.

Alloy middle-weight rare earths element can randomly comprise neodymium, and in one embodiment, REE mainly is lanthanum, cerium and neodymium.Be not wishing to be bound by theory, comprise the creep resistance that neodymium can improve alloy.Yet, also can improve castibility, especially the hot tearing resistance of alloy through the content that reduces neodymium in the alloy.When existing, the content of neodymium is the 0.5-2.0 weight % of alloy preferably, more preferably 0.5-1.5 weight %, more preferably about 1 weight %.

Multiple REE mainly comes the La mixed rare earth of other REE of self-contained lanthanum, cerium, optional neodymium, an amount of praseodymium (Pr) and trace.In another embodiment, REE can be from cerium mishmetal and pure lanthanum, so that higher with respect to cerium content lanthanum content.For the alloy that needs the low levels cerium, REE can be from the commercially pure article source of lanthanum.

Neodymium can be from above-mentioned one or both mishmetals, pure lanthanum source, didymium (neodymium-promethium alloy of high neodymium) or its arbitrary combination.

Yttrium is the optional component that can comprise.Be not wishing to be bound by theory, comprise yttrium and be considered to help melt protecting and creep resistance.Yet, also can improve castibility, especially the hot tearing resistance of alloy through the content that reduces yttrium in the alloy.When existing, the content of yttrium is 0.005%-0.5 weight % preferably, more preferably 0.01-0.4 weight %, more preferably 0.05-0.3 weight %, especially preferably 0.1-0.2 weight %.

The lanthanum in REE source or the mishmetal of cerium comprise yttrium alternatively.Thereby yttrium content is also from these mishmetals.Also can there be or exist the compsn of mishmetal in yttrium content from pure yttrium source, magnesium-yttrium mother alloy or its arbitrarily.

Gadolinium is the optional composition that can comprise.Be not wishing to be bound by theory, comprise creep resistance and oxidation-resistance that gadolinium is considered to help melts.Add gadolinium and can be used as the replacement that adds yttrium.Yet, add gadolinium and also can carry out simultaneously with the adding of yttrium.When existing, the preferred 0.005%-0.5 weight of the content of gadolinium %, more preferably 0.01-0.4 weight %, more preferably 0.05-0.3 weight %, especially preferably 0.1-0.2 weight %.

Preferably, comprise at least 94.0% magnesium, more preferably 95-96% magnesium, and most preferably about 95.3-95.7% magnesium according to alloy of the present invention.

The content of zinc is 0.2-0.8 weight %, preferred 0.2-0.6%, more preferably about 0.4%.

The preferred 0.05-0.15 weight of the content of aluminium %, more preferably 0.08-0.12 weight %, more preferably about 0.1 weight % is not wishing to be bound by theory, and comprises the creep properties that these a spot of aluminium are considered to improve alloy in the alloy of the present invention.

Beryllium content is 0-25ppm.Although, when having yttrium, be preferably and do not contain beryllium because yttrium has the effect similar with beryllium when a small amount of when yttrium exists; But when beryllium exists, the preferred 4-20ppm of beryllium content, more preferably 4-15ppm, more preferably 6-13ppm is such as 8-12ppm.When existing, beryllium can pass through aluminium-beryllium mother alloy usually, introduces such as the Al-5%Be alloy.Be not wishing to be bound by theory, comprise the die casting property that beryllium is considered to improve alloy.Once more, be not wishing to be bound by theory, comprise the oxidation-resistance that beryllium also is considered to improve molten alloy, especially improve the reservation degree of alloy middle-weight rare earths element antagonism oxidation loss.

The zirconium that adding can make iron from molten alloy, be precipitated out can reduce the content of iron.Therefore, indicated here zirconium content is remaining zirconium content.Yet, it should be noted that zirconium can be introduced in two different stepss.One is in the manufacturing processed of alloy, and another is after alloy remelting and before the casting.Preferably, zirconium content is the required minimum quantity of iron decreasing ratio that reaches satisfied.Usually, zirconium content is less than 0.1%.

Manganese is the optional a kind of composition of alloy.When existing, manganese content is typically about 0.1%.

Calcium (Ca) is a kind of optional component, especially controlling through the blanketing gas environment under the situation of the melts that adequately protects, can select the calcium that contains.This situation is the situation that casting technique does not comprise an airtight system.

Ideally, the content of incidental impurity is 0, almost is impossible but can understand this.Therefore, the content of preferred incidental impurities is less than 0.15%, more preferably is less than 0.1%, more preferably is less than 0.01%, especially preferably is less than 0.001%.

Aspect second, the invention provides a kind of power pack that makes according to the alloy of first aspect present invention through Hpdc that can be used for oil engine.

Aspect the 3rd, the invention provides a kind of parts of the automatic transmission system that forms by alloy according to first aspect present invention.

The parts of transmission system can be the parts of power pack or mover, such as shell, sump or support.

The parts of transmission system can be gear box casing or other wheel box parts.

Last mask body has been mentioned transmission system, but it should be noted that alloy of the present invention also can be used in other high temperature application and in the lower temperature application.Also specifically mentioned HPDC above, but it should be noted that alloy of the present invention can also comprise that the moulding of semi-solid-state metal thixotropic injection, thixotroping moulding, permanent mold casting and sand mold casting casts through the technology outside the HPDC.

Aspect the 4th, the invention provides a kind of goods that form by alloy according to first aspect present invention

Description of drawings

Fig. 1 is the comparison diagram of alloy A to the creep curve of alloy F (being included) that under 177 ℃ of the same terms with 90MPa, records;

Fig. 2 is the comparison diagram of the creep curve of the alloy G that under 177 ℃ of the same terms with the tension load of 90MPa, records and H, alloy X;

Fig. 3 (a) is for having three little dischargers (referring to the left-hand side of picture) and the picture of the castibility punch die part of the door (referring to the right-hand side of picture) of three parts being associated;

Fig. 3 (b) is the picture on the blank surface of the HPDC part foundry goods that made by alloy H of the present invention;

Fig. 4 is the comparison diagram of the subsurface defect structure of the foundry goods part (referring to Fig. 2) of under identical processing conditions, being cast by (a) of the present invention alloy I, (b) alloy J and (c) alloy H;

Fig. 5 is the similar temperature of alloy I and H and the graphic representation of solid rate (fs), and this graphic representation is based on the Gulliver-Scheil model algorithm, and the calphad of accomplishing every kind of independent REE of blended with supposition obtains;

Fig. 6 is variation alloys (a) I and (b) comparison diagram of the surface quality of H;

Fig. 7 is the alloy K that under 177 ℃ of the same terms with 90MPa, the records comparison diagram to the creep curve of alloy P (being included).

Embodiment

Embodiment 1

The alloy for die casting of the modification of a kind of high Nd have following composition:

1.8wt.％Nd

0.7wt.％Ce

0.4wt.％La

0.6wt.％Zn

Surplus Mg

Through soaking the cylinder that diameter 10mm hole is arranged at the bottom, this alloy takes out from the special-purpose blanketing gas protection that is called AM-cover.Press the speed of 2l/min at the cylinder top and introduce dry air.Degree of depth 50mm place in the molten alloy is immersed in the bottom of cylinder, observes the situation of melt surface.

For the alloy of this high Nd, new almost blackening at once of melt surface, and incendiary magnesium can occur in a large number after the short time.

The yttrium that in melts, adds 53ppm through 43% yttrium-57% magnesium mother alloy can greatly change the oxidation-resistance of melts.When cylinder inserts in the melts, melt surface will keep lightness and glossiness 5 seconds before the point-like burning occurring.When adding the 250ppm yttrium, flame resistant generation property will be very excellent.

When the adding gadolinium replaces yttrium in melts, also can obtain similar effect.The gadolinium that adds 310ppm is enough to make delay 60 seconds of cylinder test dotted burn off, but still effective not as yttrium on this purpose.

The high lanthanum modification that has been found that alloy has and high Nd modification different characteristic.Test is primarily aimed at the oxidation-resistance of the high La modification of alloy to be carried out, and this alloy comprises:

1.6wt.％La

0.9wt.％Nd

1.1wt.％Ce

0.6wt.％Zn

Surplus Mg

Reuse above-mentioned cylinder test.When melts being taken out from the protection environment and put into dry air, alloy keeps lightness and glossiness, the sign of equal non-oxidation or burn off in 40 seconds.This alloy has and the similar melts protection feature of high Nd modification alloy phase that has added the 50-100ppm yttrium.Need this high La type alloy, not add yttrium from melts protection purpose.

Embodiment 2

Prepared ten kinds of alloys, and following table 1 shows the chemical analysis of alloy.Add REE with the cerium base mishmetal (comprising cerium, lanthanum and some neodymiums) and the mode of element lanthanum and neodymium.Yttrium and zinc add with their element form.Beryllium adds with aluminium-beryllium mother alloy form.Aluminium can this mother alloy and the form of aluminium element add, perhaps do not add beryllium and only the form of addition element aluminium add.Zirconium adds through the special-purpose Mg-Zr mother alloy that is called AM-cast.Except incidental impurity, the alloy surplus is magnesium.During the preparation of alloy, use the melts treatment scheme of standard.

Alloy	wt.％ Nd	wt.％ Ce	wt.％ La	wt.％Y	wt.％ Zn	ppm Be	wt.％ Al	ppmFe	Wt.% Zr (always)
										A	1.47	0.49	1.71	＜0.005	0.59	＜1	0.008	7	0.097
B	1.50	0.50	1.73	0.52	0.61	＜1	0.008	8	0.080
										C	1.35	0.47	1.70	0.037	0.60	＜1	0.030	6	0.052
D	1.34	0.46	1.73	0.033	0.61	＜1	0.055	5	0.040
										E	1.33	0.46	1.73	0.027	0.61	＜1	0.10	3	0.018
F	1.38	0.47	1.73	0.016	0.61	＜1	0.59	7	0.018
										G	0.88	1.13	1.87	＜0.01	0.41	4	0.07	13	NA
H	0.84	1.13	1.84	0.23	0.46	12	0.05	19	NA
										I	1.62	0.66	0.37	＜0.005	0.50	2	0.02	12	NA
J	1.69	0.28	0.68	＜0.005	0.43	3	0.05	22	NA

The alloy of table 1-preparation (NA: do not have and analyze)

Fig. 1 shows the creep result at 177 ℃ of alloy A when the 90MPa, B, C, D, E and F.This group creep curve shows that the composition variation has great influence to creep properties in the alloy of the present invention.Control alloy (alloy A) demonstrates less relatively creep resistance under specified experiment condition, in experiment, early get into tertiary creep (＜50 hours), finishes with 1.3% strain when testing when stopping in 600 hours.This with before other not comprise the Al/Be additive consistent with the result of the variation alloys of carrying out melts protection.

The adding yttrium (～0.05wt.%) can greatly improve creep response (alloy B).Though alloy A almost realizes 0.1% strain in the identical time with alloy B, be respectively 62 hours and 60 hours, it is much then slow that tertiary creep takes place in the experiment of alloy B.

The adding of small amount of aluminum (～0.03wt.%) can obtain the improving very significantly of creep response (alloy C).This alloy all can't arrive 0.1% strain up to～500 hours under specified experiment condition, and look and also can't arrive tertiary creep up to the time that experiment finishes (600h).When add small amount of aluminum (～0.06wt.%) time, can be observed bigger improvement the (alloy D) of creep properties, its time length in test can't arrive 0.1% strain (0.04% strain after 600 hours).Further improve aluminium content (alloy E ,～0.1wt.%) time, creep resistance begins to descend (～190 hours time 0.1% strain), though this also is considered to preferably.At last, significantly improve aluminium content (alloy F ,～0.6wt.%) will thoroughly worsen the creep response of alloy.Under specified experiment condition, alloy F is considered to have the creep resistance of non-constant.These results prove that aluminium is the microalloy additive of the excellent creep properties of a kind of important acquisition.

Fig. 2 shows alloy G and H 177 ℃ of creep results during with 90MPa.Alloy G and H all make tertiary creep delay to the extended period that has exceeded test.Fig. 2 shows the creep resistance of comparing alloy H with the alloy X according to the WO2006/105594 preparation, and alloy H has the composition of following weight part:

0.68% zinc,

1.89% neodymium,

0.56% cerium,

0.33% lanthanum,

＜0.005% yttrium,

0.05% aluminium,

＜5ppm iron,

The 12ppm beryllium,

Surplus is magnesium except incidental impurity.

In 20 and 177 ℃ air, measure tensile properties with the Instron universal testing machine according to ASTM E8.Sample kept before test 10 minutes at room temperature.Test sample all has circular xsect (5.6mm diameter), and gauge length is 25mm.

Table 2 shows the stretch test result of each alloy sample.

Table 2-tension test data

It should be noted that alloy G and alloy H especially all have extraordinary castibility.The work range of sound casting that can obtain these two kinds of alloys is wideer than above-mentioned alloy X.In order to obtain good casting quality, alloy needs less susceptibility to avoid hot tearing, good dress module feature and less susceptibility to avoid in the cross streams peak of punch die, forming defective.

Adopt the castability test punch die to assess the castibility of the alloy on a large scale in the Hpdc (HPDC).Fig. 3 shows the foundry goods that this punch die makes.This Stamping Die Design must have uses this punch die to be very difficult to make the complicated shape of the high pressure die castings of good quality.Fig. 3 (a) shows the passage (being also referred to as " passage (runner) " in the prior art) of three part gating systems on the foundry goods right-hand side, and molten alloy gets in the punch die through this passage.Can see " discharger " at opposition side (left-hand side) to the passage of foundry goods.Discharger and passage all are blocked after casting.

Come the foundry goods of alloying H with the castability test punch die.Fig. 3 (b) shows the black skin quality of the foundry goods of alloy H.

Embodiment 3

The castability test punch die of mentioning with above embodiment 2 is through Hpdc casting alloy I, J and H (referring to table 1, embodiment 2), in order to the effect to the alloy castibility of research lanthanum and cerium.

Fig. 4 shows (a) alloy I, (b) the subsurface defect structure on the foundry goods same section of alloy J and (c) alloy H.The internal cracking that has maximum after alloy I (0.66 weight % cerium, 0.37 weight % lanthanum) is considered to cast.Ratio through changing lanthanum and cerium among the alloy J (0.68 weight % lanthanum, 0.28 weight % cerium) can find out from Fig. 4 (b) that to greater than 1: 1 the amount of internal cracking is able to minimizing, has improved the total quality of foundry goods.The improvement of another castibility occurs on the alloy H; It has volume more lanthanum and cerium (1.7 weight % lanthanums, 1.1 weight % ceriums) and lanthanum and cerium ratio greater than 1: 1 with the neodymium content (being in a ratio of 0.7 weight % neodymium) that has reduced with 1.69 weight % among 1.62 weight % neodymiums and the alloy J among the alloy I.The foundry goods of alloy H is not almost found internal cracking.It can also be seen that from Fig. 4 (c) alloy H has the good internal flow defective formation and the resistance of hot tearing.

Be not wishing to be bound by theory; Can explain the possible reason that second observations forms referring to Fig. 5; Fig. 5 shows the curve of the temperature of alloy I and H with respect to solid rate; This curve is based on the Gulliver-Scheil model algorithm, and the calphad of utilizing supposition to be blended in magnesium in the alloy and the REE that each is independent obtains.Can find that the alloy H that lanthanum content is higher than alloy I has littler freezing range.Known this will reduce the susceptibility that hot tearing appears in alloy.Alloy H also has the eutectiferous amount above alloy I.This is to be confirmed by the alloy that the final section that occurs in uniform temp is solidified.For alloy H, I compares with alloy, this situation will appear at bigger fractional alloy and and the more macrocyclic time on.This also will reduce the susceptibility that hot tearing appears in alloy H.It should be noted that changing coagulating property aspect the susceptibility that reduces alloy and hot tearing occurs, lanthanum is more more effective than cerium.This is because for the cerium alloy identical with the total amount of lanthanum content, more most eutectic occurred in the rich lanthanum alloy that solidifies, and eutectiferous temperature is higher.

Once more, be not wishing to be bound by theory, compare with using alloy I, the reduction of the flow line when Hpdc uses alloy H also possibly be to cause the reason that internal cracking reduces among the alloy H., the fluid that gets into the molten alloy of punch die from passage forming flow line during the HPDC when meeting the fluid of other passages.The oxidation of alloy occurs in these fluidic surface, and these fluids meet and at the inner curve that flows to that forms visual oxide alloy of foundry goods.Be not wishing to be bound by theory,, so think that the high yttrium content among the alloy H is the reason that causes this phenomenon because it can improve from the recovery of the beryllium of mother alloy additive and the oxidation ratio that influence beryllium in the molten alloy.

Fig. 6 show (a) alloy I and (b) the HPDC foundry goods of alloy H improvement outward appearance, wherein high lanthanum and beryllium content alloy (alloy H) have the more outward appearance of improvement.

Embodiment 4

Make all the other 5 kinds of alloys, in order to the effect of research neodymium additive.According to the technology alloying described in the embodiment 2.Following table 3 provides the chemical analysis of these other alloys (K-P).

Alloy	wt.％ Nd	wt.％ Ce	wt.％ La	wt.％ Y	wt.％ Zn	ppm Be	wt.％ Al	ppm Fe	Wt.% Zr (always)
										K	0.01	0.52	1.49	0.05	0.41	＜1	0.05	73	0.0
L	0.22	0.84	1.80	0.01	0.41	＜1	0.023	108	0.0
										M	0.45	0.53	1.52	0.03	0.41	＜1	0.05	86	0.0
N	0.73	0.46	1.42	0.02	0.42	＜1	0.04	107	0.0
										P	0.93	0.39	1.42	0.04	0.42	＜1	0.032	121	0.0

The alloy that table 3 makes

Fig. 7 show 177 ℃ when the 90MPa alloy K to the creep result of alloy P.As can beappreciated from fig. 7, the increase of neodymium content can improve creep response (referring to table 3) in the alloy.Alloy K, alloy M, alloy N and alloy P also have very similarly composition on other alloying elements except neodymium content.This curve has been depicted as the creep response that is applicable to that more high temperature is used, and the neodymium content in the alloy should be greater than about 0.5wt.%.

Claims

1. Magnuminium is grouped into by the one-tenth of following weight part:

The 2-5% REE, wherein this alloy comprises rare-earth elements of lanthanum and cerium, and lanthanum content is greater than cerium content;

0.2-0.8% zinc;

0-0.15% aluminium;

0-0.5% yttrium or gadolinium;

The 0-0.2% zirconium;

0-0.3% manganese;

0-0.1% calcium;

The 0-25ppm beryllium; And

Surplus is magnesium except incidental impurity.

2. Magnuminium according to claim 1, wherein in this alloy the ratio of lanthanum and cerium greater than 1: 1.

3. Magnuminium according to claim 1 and 2, wherein this alloy also comprises rear earth element nd.

4. Magnuminium according to claim 3, wherein the lanthanum content of this alloy is greater than neodymium content.

5. according to claim 3 or 4 described Magnuminiums, wherein the cerium content of this alloy is greater than neodymium content.

6. according to each described Magnuminium of claim 3-5, wherein the total content of the lanthanum of this alloy and cerium is greater than neodymium content.

7. according to each described Magnuminium of claim 3-6, wherein the neodymium content of this alloy is 0.5-2.0% by weight.

8. according to each described Magnuminium of claim 3-6, wherein the neodymium content of this alloy is 0.5-1.5% by weight.

According to before the described Magnuminium of each claim, wherein the total content of the lanthanum of this alloy and cerium is 1.5-3.5% by weight.

According to before the described Magnuminium of each claim, wherein the total content of the lanthanum of this alloy and cerium is 1.8-3.0% by weight.

11. according to before the described Magnuminium of each claim, wherein the total content of the lanthanum of this alloy and cerium is 2.0-2.8% by weight.

12. according to before the described Magnuminium of each claim, wherein yttrium content is 0.005-0.5% by weight.

13. according to before the described Magnuminium of each claim, wherein gadolinium concentrations is 0.005-0.5% by weight.

14. according to before the described Magnuminium of each claim, wherein this alloy is made up of at least 94% magnesium by weight.

15. according to before the described Magnuminium of each claim, wherein zinc content is 0.2-0.6% by weight.

16. according to before the described Magnuminium of each claim, wherein aluminium content is 0.05-0.15% by weight.

17. according to before the described Magnuminium of each claim, wherein zirconium content is less than 0.1% by weight.

18. according to before the described Magnuminium of each claim, wherein beryllium content is 8-12ppm by weight.

19. according to before the described Magnuminium of each claim, wherein manganese content is near 0.1% by weight.

20. according to before the described Magnuminium of each claim, incidental impurity is less than 0.15% by weight in its interalloy.

21. power pack of making through Hpdc by the described alloy of above-mentioned each claim that can be used as oil engine.

22. parts by the transmission system that forms like each described alloy of claim 1-20.

23. one kind by the goods that form like each described alloy of claim 1-20.