CN1602368A - Aluminum-silicon alloys having improved mechanical properties - Google Patents
Aluminum-silicon alloys having improved mechanical properties Download PDFInfo
- Publication number
- CN1602368A CN1602368A CNA028217861A CN02821786A CN1602368A CN 1602368 A CN1602368 A CN 1602368A CN A028217861 A CNA028217861 A CN A028217861A CN 02821786 A CN02821786 A CN 02821786A CN 1602368 A CN1602368 A CN 1602368A
- Authority
- CN
- China
- Prior art keywords
- silicon
- average
- nodularization
- phase component
- eutectic phase
- 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.)
- Granted
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
- C22C21/04—Modified aluminium-silicon alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
Landscapes
- Chemical & Material Sciences (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Investigating And Analyzing Materials By Characteristic Methods (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Conductive Materials (AREA)
- Silicon Compounds (AREA)
- Heat Treatment Of Articles (AREA)
- Crystals, And After-Treatments Of Crystals (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Ceramic Products (AREA)
- Powder Metallurgy (AREA)
- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
- Laminated Bodies (AREA)
Abstract
The invention relates to a heat treatment method for articles composed of substantially Al-Si alloys that contain a eutectic phase, and to articles that consist of these alloys. In order to improve the ductility of the material or to increase the elongation after fracture, an annealing process is carried out in the form of shock annealing, said process comprising the following steps: rapidly heating the material to an annealing temperature of from 400 to 555 DEG C, maintaining it at this temperature for a period of not more than 14.8 minutes, force-cooling it, and then aging the article. The inventive article comprises spheroidized silicon precipitations in the eutectic phase portion with an average plane of section ASi of less than 4 mu m2 and/or an average distance between the silicon particles lambda Si of less than 4 mu m and/or an average spheroidization density xi Si of greater than 10.
Description
The present invention relates to a kind of method that is used to improve aluminium-silicon-alloy mechanical performance.In particular, the present invention relates to a kind of heat treating method that improves object materials ductility, this object is made of cast alloys that has the eutectic phase component or plastic metal, it preferably contains modified (veredelten) or purified aluminium-element silicon, other alloying elements and/or impurity element are also randomly arranged, and this object then carries out the timeliness effect after anneal.
The invention still further relates to a kind of object, this object is to be made of the aluminium-silicon that has the eutectic phase component-alloy, it preferably has at least a modified element (Veredelungselement), randomly also contain magnesium and other alloys and/or impurity element, eutectic phase component wherein mainly is made of α-Al matrix and silicon precipitation.
Aluminium and silicon form a kind of simple eutectic system, and wherein, Si concentration is that eutectoid point appears when being 577 ℃ in 12.5 weight % and temperature.
By addition element magnesium and through thermal treatment and formed Mg
2The Si precipitation can significantly improve the intensity of material, and when magnesium was about 550 ℃ in temperature, the maximum amount that can be dissolved in α-Al matrix was 0.47 weight %.
Can solidify to eutectic residual melt by cooling Al-Si-Mg melt, wherein silicon is with flaky thick form precipitation.Prior art for a long time is to mix sodium or strontium in this alloy, stops the growth of silicon crystal when solidifying thus, is referred to as modifiedly or refining, can improve mechanical property, particularly extension at break unlimitedly.
Basically can influence the mechanical property of aluminium alloy work in-process or object by heat treating method, by European standard EN515 definition as-heat-treated condition.According to standard, in steady state letter F=production status, T=is heat treated.The numerical table that each as-heat-treated condition is arranged after by tee shows.
In addition, below represent the following as-heat-treated condition of material with dummy suffix notation in the explanation:
F is a production status
T5 is from the quenching of production temperature and carries out the thermal life effect
T6 is liquation annealing and carries out the thermal life effect
T6x is according to thermal treatment of the present invention
T4x is according to thermal treatment of the present invention
When using the object that constitutes by the Al-Si alloy for being fit to market demand or industry, material property is important on the one hand, but production cost or economic conditions also are important on the other hand, because anneal under high temperature more for a long time, and essential during long term annealing to pass through the indispensable aligning process (Nacchrichtvorg nge) that so-called gravity creep carries out be expensive.
Basically can confirm that the Al-Si alloy of F state has little strength of materials value R mostly
pWith higher extension at break coefficient A.
At as-heat-treated condition T5, i.e. the quenching of production temperature and carry out the thermal life effect is for example in the time of 155 ℃ to 190 ℃, during 1 to 12 hour, though reach the intensity level R of sample
pHigher, but extension at break coefficient A is lower.
The as-heat-treated condition of corresponding T6, promptly for example liquation carries out the thermal life effect subsequently 540 ℃ of annealing temperatures 12 hours, and F compares with state, and under the situation that the ductility of the extension at break of sample or material equates substantially, but the intensity of material improves greatly.For example, the liquation annealing time is long, and the magnesium atom in the material is advantageously spread, and therefore, after object quenching and thermal life are used, forms the Mg that distributes very evenly in α-Al matrix
2The Si precipitation, this precipitation improves the strength of materials fatefully.
But, during high temperature liquation is carried out long term annealing and handle the shortcoming that exists, as mentioned above, i.e. Bu Fen gravitational creep and expensive temperature-time degree of treatment.Therefore, from economically, many-sided consideration on the maximum intensity that reaches material and the good ductility is not selected T6, and is selected the treated state T5 of object.Randomly must compensate the low strength of materials that determines because of T5 by the structure that changes member.
At this situation, the invention provides a kind of novel, economic heat treating method, this method can significantly improve the ductility of material, compare with T6, the strength of materials is not had big interference, perhaps compare, obtain showing the higher ductility and the higher strength of materials with T5.
In addition, the purpose of this invention is to provide a kind of microtexture that begins the object of the favourable mechanical property of materials of having of described class.
The purpose of present method is achieved in that promptly with impact type annealing carries out the liquation anneal, comprising: being heated rapidly to 400-555 ℃ annealing temperature, is 14.8 minutes in the soaking time the longest of this temperature, forces to be cooled to room temperature basically then.
Advantage of the present invention mainly is, adopts simple high temperature-short annealing to reach the ductility value of object maximum.In addition, so-called impact type anneal makes the deformation of member or deformation of body reduce so randomly not need self aligning up to not taking place.Anneal also has higher economic value rapidly, and can for example by continuous furnace, incorporate in the production process with plain mode.At least can regulate the strength of materials by a kind of adjusting process of thermal life effect subsequently.Be less than 6.8 minutes if can be advantageously provided the hold-time of impact type anneal, preferred 1.7 to randomly maximum 5 minutes, then improves ductility to greatest extent under the dominant situation of the quantity of Al-Si alloy.
Carry out the thermal life effect of object after the impact type annealing, being about to it, to place 1-14 hour under 150-200 ℃ of temperature be favourable.
If impact type annealing back also is favourable to material technology then carrying out the timeliness effect of object under the room temperature with the cold ageing effect substantially.
Another object of the present invention is such realization, though the nodularization of the silicon of eutectic phase component precipitation, its average cross section A
SiLess than 4 μ m
2
Below the formula in cross section is calculated in expression,
Parametric representation wherein:
A
SiThe average area of=silicon particle (μ m
2)
The average area of the silicon particle of every photo of A=(μ m
2)
N=measures number of times
The advantage of this microtexture mainly is, because sedimentary nodularization of silicon and purifying have reduced the initial crack of material basically, and improved material ductility.In other words, nodularization and small size make brittle eutectic silicon have suitable form, fundamentally cause the higher extension at break value of material.Stress concentration when having reduced mechanical load on the Si-Al phase interface.Also find the transgranular fracture of material in the test, therefore demonstrate the highest ductility.
If the silicon of eutectic phase component precipitation is nodularization, and average cross section is less than 2 μ m
2, then the high extension at break value for complete processing and material is favourable.
Pointed as R﹠D work, if be implemented as follows the present invention, promptly be defined as foursquare survey area divided by the mean free path λ between the silicon particle of the eutectic phase component of the root of the number of its contained silicon particle according to goal of the invention
SiValue less than 4 μ m, preferably less than 3 μ m, especially preferably, then when minimum peak stress, reach special uniform stress distribution in the material of load, because the spacing of small area silicon particle has mainly influenced the rheological property of material under the corresponding stressed condition less than 2 μ m.Calculate the average headway λ of silicon particle once more with following formula
Si
λ
SiThe average headway of=silicon particle
A
Square=foursquare reference plane (μ m
2)
N
SiliconThe number of=Si particulate
N=measures the number of photo
The liquation annealing of prior art is the long term annealing at 2 to 12 hours, so that the alloy compositions diffusion of sclerization is arranged, and be enriched in the mixed crystal, though also cause the side effect of nodularization silicon particle, but because annealing for a long time, these Particle Distribution are very big and coarse, and this fracture property to material is unfavorable.According to the present invention, surprisingly,, can in the short period of time of several minutes, make eutectic silicon crystal lattice nodularization, thereby obtain favourable material microstructure by impact type annealing rapidly.At this, importantly impact type annealed temperature should be high as far as possible, but should be lower than minimum fusion phase temperature, preferably low 5 to 20 ℃.
Make silicon particle carry out the growth of controlled diffusion with the prolongation annealing time, make originally favourable high nodularization density ξ this moment
SiDiminished.
Find when realizing the object of the invention, if be defined as per 100 μ m
2The average nodularization density ξ of the number of the eutectic silicon particle of nodularization
SiGreater than 10, and preferred 20, and then the ductility of Al-Si alloy object is the highest.
ξ
SiThe average nodularization density of=eutectic silicon particle
N
SiliconThe number of=Si particulate
A=reference plane (μ m
2)
N=measures the number of photo
Related formula explanation as previously mentioned.
The result shows that the every kind of Al-Si alloy that contains the eutectic phase basically all can have structure of the present invention, and the object of Xing Chenging has high material ductility value thus.If be equipped with object, all be effective especially then to improving quality and improving extension at break with the thixo casting legal system.
Further specify the present invention by test result and photo below:
Fig. 1 bar graph: the mechanical value that depends on the material of as-heat-treated condition
Fig. 2 is same
The REM photo of Fig. 3 section
Fig. 4 is same
The relation of sedimentary average area of Fig. 5 Si and annealing time
Fig. 6 is same
Mean free path between Fig. 7 Si particulate
The average nodularization density of Fig. 8
Fig. 9 bar graph: the mechanical property of the material of different al-Si alloy
The numerical value of table 1 Fig. 9
Table 1
???????????F | ???????????T5 | ?????????T6×3 | ?????????????T6 | |||||
Scheme | ???Rp[MPa] | ??A[%] | ???Rp[MPa] | ?A[%] | ???Rp[MPa] | ??A[%] | ???Rp[MPa] | ????A[%] |
????Alsi7Mg03 | ????121.7 | ??13.0 | ????167.5 | ??9.9 | ????228.5 | ??16.7 | ????259.8 | ????10.6 |
????Alsi7Mg05 | ????143.9 | ??10.4 | ????175.8 | ??9.3 | ????240.2 | ??13.9 | ????311.7 | ????9.1 |
????Alsi7Mgx | ????159.8 | ??8.3 | ????197.2 | ??6.8 | ????265.2 | ??10.1 | ????322.9 | ????7.6 |
????Alsi6Mgx | ????159.7 | ??10.2 | ????195.3 | ??7.8 | ????250.6 | ??8.9 | ????318.6 | ????6.5 |
????Alsi5Mgx | ????154.9 | ??10.1 | ????189.6 | ??7.5 | ????240.6 | ??9.5 | ????313.6 | ????8.7 |
????+Mn04 | ????157.1 | ??10.6 | ????183.7 | ??6.9 | ????252.7 | ??7.4 | ????322.7 | ????7.6 |
????+Mn08 | ????154.8 | ??9.9 | ????184.0 | ??6.6 | ????255.9 | ??6.7 | ????324.4 | ????4.9 |
????AlSi5Mgxx | ????211.7 | ??3.5 | ????256.4 | ??2.5 | ????242.1 | ??5.1 | ????291.6 | ????5.3 |
Fig. 1 represents the R of the sample of the test component that made by alloy A lSi7Mg0.3 with bar graph
P0.2Yield point value and extension at break value A, this alloy component prepares with thixo casting method (Thixocastingverfahren).The value of material hot treatment state T6 (12 hours 540 ℃+4 hours 160 ℃) with adopt the inventive method at 1 minute (T6 * 1) back of 540 ℃ of following impact types annealing, 3 minutes (T6 * 3) back and the T6 that obtained after (T6 * 5) in 5 minutes * compare.All sample carries out thermal life effect (4 hours) under 160 ℃.Tensile test result shows that the extension at break value of the sample after the impact type anneal is obviously higher, compares with T6, and state T6 * 3 cause A to raise about 60%.
The state value that has compared the sample of same manufacturing once more with bar graph among Fig. 2 is the R of F, T4 * 3, T5, T6 * 3 and T6
P0.2With extension at break A.Show that more once more the extension at break value obviously raises.As can be seen from Figure 2, in order to obtain outstanding extension at break performance of the present invention, impact type annealing is after 3 minutes, cold ageing effect (T4 * 3) or the thermal life effect (T6 * 3) that can carry out material.
Fig. 3 and Fig. 4 represent the sedimentary electron scanning micrograph of Si.Note image pickup method and evaluation method:, must use suitable binary photo for can quantitative evaluation Photomicrograph (Schliffbilder).Take with scanning electronic microscope, reach 2 hours up to annealing time, the solution with 99.5% water and 0.5% hydrofluoric acid corroded abrasive disc 30 seconds in advance afterwards.Anneal after 4 hours, corrode abrasive disc with Keller solution, and with optics microscope photographing photo.All photos are with Adobe Photoshop 5.0 progressive number aftertreatments, and with picture analyzing program Leica Qwin V2.2 evaluation, wherein Zui Xiao area of detection is 0.1 μ m
2Fig. 3 shows the materials A lSi7Mg0.3 of conventional T6-annealing after 12 hours that takes with REM.Fig. 4 provides the microtexture of the material of impact type anneal after 3 minutes again.Silicon precipitation obviously nodularization (Fig. 4) after short period of time, behind the long annealing time self controlled diffusion grow (Fig. 3) be conspicuous.
Fig. 5 and Fig. 6 depend on the silicon particle average cross section A of 540 ℃ of following annealing times when representing the abrasive disc test
SiDescription according to Fig. 4 can obviously find out, the average cross section of silicon particle that with the particle size is feature is along with logarithmic time shaft increases.From the detailed description of Fig. 6, can observe the increase of the average silicon area that in initial 60 minutes, causes owing to diffusion.Depend primarily on the initial size of Si particulate in the eutectic mixture along with the silicon particle mean sizes of annealing time increase.Owing to there is the special good modified silicon that distributes with purification under described situation, accidental can shorten the time under the modified not so good situation of silicon particle (particulate is bigger when showing beginning), interior crucial average silicon area A of this time
SiReach about 4 μ m
2
The test-results of Fig. 7 represents to depend on the variation of average headway of the Si particulate of annealing time.The average headway that can obviously observe the Si inclusion increases.
At last, Fig. 8 represents to depend on the average nodularization density ξ of annealing time
SiDecline.Average nodularization density has begun rapid decline in the time of 1.7 minutes, from value ξ
Si<10 are caused tangible ductility loss.During higher anneal temperature, just reach this value after 14 to 25 minutes, for dominant high extension at break value, density value is predetermined greater than 20.
Fig. 9 provides the elongation border of described 8 the different Al-Si alloys of forming of table 1 and the observed value of extension at break again by bar graph.The material ductility of all alloys of the present invention has all increased.
Claims (11)
1. heat treating method that is used to improve the material ductility of object, this object is made of cast alloys with eutectic phase component or plastic metal, this alloy preferably contains modified or purified aluminium-element silicon, other are also randomly arranged such as magnesium, manganese, alloying element and/or impurity elements such as iron, this object then carries out the timeliness effect after anneal, it is characterized in that, carry out anneal with impact type annealing, it comprises: be heated rapidly to 400-555 ℃ annealing temperature, be preferably at least 1.7 minutes to maximum 14.8 minutes in this following hold-time of temperature, force to be cooled to room temperature basically subsequently.
2. according to the method for claim 1, it is characterized in that the hold-time of impact type anneal, preferred time range was at least 1.7 minutes to randomly maximum 5 minutes less than 6.8 minutes.
3. according to the method for claim 1 or 2, it is characterized in that, under 150 to 200 ℃ temperature, object was carried out the thermal life effect 1-14 hour after the impact type anneal.
4. according to the method for claim 1 to 3, it is characterized in that, after the impact type annealing, under the room temperature object is being carried out the cold ageing effect basically.
5. object that forms by aluminium-silicon alloy with eutectic phase component, this alloy preferably has at least a modified element, randomly also has other such as alloying element and/or impurity elements such as magnesium, manganese, iron, this object mainly by α-
AlMatrix and silicon precipitation constitute, and it is characterized in that, the silicon precipitation in the eutectic phase component is nodularization, its average cross section A
SiLess than 4 μ m
2
A
SiThe average area of=silicon particle (μ m
2)
The average area of the silicon particle of every photo of A=(μ m
2)
N=measures number of times.
6. according to the object of claim 5, it is characterized in that the silicon precipitation in the eutectic phase component is nodularization, average cross section A
SiLess than 2 μ m
2
7. object that forms by aluminium-silicon alloy with eutectic phase component, this alloy preferably has at least a modified element, randomly also has other such as alloying element and/or impurity elements such as magnesium, manganese, iron, this object mainly by α-
AlMatrix and silicon precipitation constitute, and it is characterized in that, are defined as foursquare survey area divided by the mean free path λ between the silicon particle of the eutectic phase component of the root of the number of its contained silicon particle
SiValue less than 4 μ m
λ
SiThe average headway of=silicon particle
A
Square=foursquare reference plane (μ m
2)
N
SiliconThe number of=Si particulate
N=measures the number of photo.
8. according to the object of claim 7, it is characterized in that the value of mean free path is less than 3 μ m, preferably less than 2 μ m.
9. object that constitutes by the aluminium with eutectic phase component-silicon alloy, this alloy preferably has at least a modified element, randomly also has other such as alloying element and/or impurity elements such as magnesium, manganese, iron, this object mainly by α-
AlMatrix and silicon precipitation constitute, and it is characterized in that, are defined as per 100 μ m
2The average nodularization density ξ of the number of the eutectic silicon particle of nodularization
SiGreater than 10
ξ
SiThe average nodularization density of=eutectic silicon particle
N
SiliconThe number of=Si particulate
A=reference plane (μ m
2)
N=measures the number of photo.
10. according to the object of claim 9, it is characterized in that the value of average nodularization density is greater than 20.
11. claim 5-10, the object according to claim 1--4 preparation is characterized in that it prepares with the thixo casting method.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
ATA1733/2001 | 2001-11-05 | ||
AT0173301A AT411269B (en) | 2001-11-05 | 2001-11-05 | ALUMINUM-SILICON ALLOYS WITH IMPROVED MECHANICAL PROPERTIES |
Publications (2)
Publication Number | Publication Date |
---|---|
CN1602368A true CN1602368A (en) | 2005-03-30 |
CN100366782C CN100366782C (en) | 2008-02-06 |
Family
ID=3688773
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CNB028217861A Expired - Fee Related CN100366782C (en) | 2001-11-05 | 2002-11-05 | Aluminum-silicon alloys having improved mechanical properties |
Country Status (15)
Country | Link |
---|---|
US (2) | US20050000608A1 (en) |
EP (1) | EP1442150B1 (en) |
JP (1) | JP2005508446A (en) |
KR (1) | KR20050043748A (en) |
CN (1) | CN100366782C (en) |
AT (2) | AT411269B (en) |
CA (1) | CA2465683C (en) |
DE (1) | DE50209192D1 (en) |
DK (1) | DK1442150T3 (en) |
ES (1) | ES2280578T3 (en) |
HK (1) | HK1071171A1 (en) |
HU (1) | HUP0401962A2 (en) |
PT (1) | PT1442150E (en) |
SI (1) | SI1442150T1 (en) |
WO (1) | WO2003040423A1 (en) |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8950468B2 (en) | 2007-05-11 | 2015-02-10 | The Boeing Company | Cooling system for aerospace vehicle components |
DE102008024524A1 (en) * | 2008-05-21 | 2009-11-26 | Bdw Technologies Gmbh | Method and plant for producing a cast component |
DE102011105447B4 (en) * | 2011-06-24 | 2019-08-22 | Audi Ag | Process for the production of aluminum die-cast parts |
CN107586939A (en) * | 2017-09-13 | 2018-01-16 | 中信戴卡股份有限公司 | A kind of heat treatment method for aluminium alloy casting rotation wheel |
CN109706411A (en) * | 2019-02-18 | 2019-05-03 | 东莞宏幸智能科技有限公司 | A kind of solid smelting furnace of aluminum alloy spare part production |
CN115961223A (en) * | 2022-12-19 | 2023-04-14 | 湖南中创空天新材料股份有限公司 | Method for removing residual stress |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0747807B2 (en) * | 1992-03-17 | 1995-05-24 | スカイアルミニウム株式会社 | Method for producing rolled aluminum alloy plate for forming |
JPH07166285A (en) * | 1993-06-08 | 1995-06-27 | Shinko Alcoa Yuso Kizai Kk | Hardened al alloy sheet by baking and production thereof |
JPH11613A (en) * | 1997-06-13 | 1999-01-06 | Kawasaki Steel Corp | Manufacture of aluminum alloy plate with superior molding properties and coat baking/curing properties |
US6040059A (en) * | 1997-11-18 | 2000-03-21 | Luk Gmbh & Co. | Component made of an aluminium silicon cast alloy |
US5985349A (en) * | 1998-11-12 | 1999-11-16 | Kraft Foods, Inc. | Method for manufacture of grated cheese |
DE19901508A1 (en) * | 1999-01-16 | 2000-08-17 | Bayerische Motoren Werke Ag | Process for the production of castings from aluminum alloys |
DE19925666C1 (en) * | 1999-06-04 | 2000-09-28 | Vaw Motor Gmbh | Cast cylinder head and engine block component is made of an aluminum-silicon alloy containing aluminum-nickel, aluminum-copper, aluminum-manganese and aluminum-iron and their mixed phases |
JP2001316747A (en) * | 1999-08-31 | 2001-11-16 | Asahi Tec Corp | NON-Cu CAST Al ALLOY AND HEAT TREATING METHOD THEREFOR |
JP3857503B2 (en) * | 2000-07-26 | 2006-12-13 | 大同メタル工業株式会社 | Aluminum bearing alloy |
ATE503982T1 (en) * | 2002-01-11 | 2011-04-15 | Gen Hospital Corp | DEVICE FOR OCT IMAGE ACQUISITION WITH AXIAL LINE FOCUS FOR IMPROVED RESOLUTION AND DEPTH OF FIELD |
-
2001
- 2001-11-05 AT AT0173301A patent/AT411269B/en not_active IP Right Cessation
-
2002
- 2002-11-05 EP EP02774155A patent/EP1442150B1/en not_active Expired - Lifetime
- 2002-11-05 SI SI200230502T patent/SI1442150T1/en unknown
- 2002-11-05 DE DE50209192T patent/DE50209192D1/en not_active Expired - Lifetime
- 2002-11-05 ES ES02774155T patent/ES2280578T3/en not_active Expired - Lifetime
- 2002-11-05 CN CNB028217861A patent/CN100366782C/en not_active Expired - Fee Related
- 2002-11-05 PT PT02774155T patent/PT1442150E/en unknown
- 2002-11-05 WO PCT/AT2002/000309 patent/WO2003040423A1/en active Application Filing
- 2002-11-05 JP JP2003542667A patent/JP2005508446A/en active Pending
- 2002-11-05 AT AT02774155T patent/ATE350507T1/en active
- 2002-11-05 DK DK02774155T patent/DK1442150T3/en active
- 2002-11-05 CA CA2465683A patent/CA2465683C/en not_active Expired - Fee Related
- 2002-11-05 HU HU0401962A patent/HUP0401962A2/en unknown
- 2002-11-05 KR KR1020047006793A patent/KR20050043748A/en active Search and Examination
-
2004
- 2004-05-04 US US10/837,665 patent/US20050000608A1/en not_active Abandoned
-
2005
- 2005-02-04 HK HK05100996A patent/HK1071171A1/en not_active IP Right Cessation
-
2010
- 2010-04-12 US US12/758,381 patent/US20100193084A1/en not_active Abandoned
Also Published As
Publication number | Publication date |
---|---|
EP1442150A1 (en) | 2004-08-04 |
CA2465683A1 (en) | 2003-05-15 |
CA2465683C (en) | 2011-01-18 |
JP2005508446A (en) | 2005-03-31 |
EP1442150B1 (en) | 2007-01-03 |
ATE350507T1 (en) | 2007-01-15 |
SI1442150T1 (en) | 2007-06-30 |
HK1071171A1 (en) | 2005-07-08 |
KR20050043748A (en) | 2005-05-11 |
DK1442150T3 (en) | 2007-05-14 |
DE50209192D1 (en) | 2007-02-15 |
US20050000608A1 (en) | 2005-01-06 |
US20100193084A1 (en) | 2010-08-05 |
HUP0401962A2 (en) | 2005-01-28 |
ES2280578T3 (en) | 2007-09-16 |
PT1442150E (en) | 2007-04-30 |
AT411269B (en) | 2003-11-25 |
ATA17332001A (en) | 2003-04-15 |
CN100366782C (en) | 2008-02-06 |
WO2003040423A1 (en) | 2003-05-15 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
KR100831637B1 (en) | Aluminum alloy sheet having excellent formability and paint bake hardenability | |
JP2010189750A (en) | High-strength aluminum alloy wire and rod material excellent in softening resistance and method of manufacturing the same | |
JP2007177308A (en) | High strength and high toughness aluminum alloy extruded material and forged material having excellent corrosion resistance, and methods for producing the extruded material and forged material | |
WO2019122076A1 (en) | 6xxx aluminium alloy extruded forging stock and method of manufacturing thereof | |
Hanim et al. | Effect of a two-step solution heat treatment on the microstructure and mechanical properties of 332 aluminium silicon cast alloy | |
EP0008996B1 (en) | Process for heat-treating aluminium-copper-magnesium-silicon alloys | |
CA2013270A1 (en) | High-modulus, high-mechanical strength al-based alloy and production process | |
JP2001517735A (en) | Aluminum alloy and heat treatment method thereof | |
JP2001059124A (en) | Al-Mg-Si ALUMINUM ALLOY COLD FORGED PART EXCELLENT IN APPEARANCE QUALITY AND ITS PRODUCTION | |
US20100193084A1 (en) | Aluminum-silicon alloys having improved mechanical properties | |
JPH0995750A (en) | Aluminum alloy excellent in heat resistance | |
US20230357889A1 (en) | Method For Manufacturing Aluminum Alloy Extruded Material | |
JP4712159B2 (en) | Aluminum alloy plate excellent in strength and corrosion resistance and method for producing the same | |
US20230357902A1 (en) | Method For Manufacturing Aluminum Alloy Extruded Material With High Strength And Excellent In SCC Resistance And Hardenability | |
JPS58167757A (en) | Preparation of al-mg-si alloy for processing excellent in corrosion resistance, weldability and hardenability | |
JP3516566B2 (en) | Aluminum alloy for cold forging and its manufacturing method | |
WO2002097148A2 (en) | Aluminum alloys and methods of making the same | |
JPH06340940A (en) | Aluminum alloy sheet excellent in press formability and baking hardenability and its production | |
JPH01152237A (en) | Aluminum alloy material for engine member | |
Mroczka et al. | 2017A aluminum alloy in different heat treatment conditions | |
JP2023548476A (en) | Improved 6XXX aluminum alloy | |
CN114318183A (en) | High-plasticity aluminum alloy part and preparation method thereof | |
CN114293117A (en) | High-strength aluminum alloy product and preparation method thereof | |
KR102012952B1 (en) | Aluminium alloy and manufacturing method thereof | |
JPS62207842A (en) | High strength aluminum alloy |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
C06 | Publication | ||
PB01 | Publication | ||
C10 | Entry into substantive examination | ||
SE01 | Entry into force of request for substantive examination | ||
C14 | Grant of patent or utility model | ||
GR01 | Patent grant | ||
C17 | Cessation of patent right | ||
CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20080206 Termination date: 20121105 |