CN100562595C - High hardness aluminium profiled sheeting and the method for producing described plate - Google Patents
High hardness aluminium profiled sheeting and the method for producing described plate Download PDFInfo
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- CN100562595C CN100562595C CNB2005800339626A CN200580033962A CN100562595C CN 100562595 C CN100562595 C CN 100562595C CN B2005800339626 A CNB2005800339626 A CN B2005800339626A CN 200580033962 A CN200580033962 A CN 200580033962A CN 100562595 C CN100562595 C CN 100562595C
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- 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
Abstract
The profiled sheeting of aluminium deformation alloy, this alloy comprises by weight percentage: Si 1.4-2.1, Mn 0.8-1.2, Cu 0.45-0.9, Mg 0.7-1.2, Ti＜0.15, Zn＜0.4, Fe＜0.7, one or more among Zr, Cr, the V, every kind＜0.25, accidental element and impurity, every kind＜0.05, total amount＜0.25, surplus is an aluminium, and has the thickness greater than 0.6mm, and has the hardness that is higher than 105HB at the T6 state.
Description
The present invention relates to the profiled sheeting (moulding plate) of aluminium deformation alloy.The invention still further relates to the method for producing described profiled sheeting.
In the tool palette and the profiled sheeting market of blowing that is used for rubber and plastics and thermoforming, when keeping gratifying wear resistance and repairing weldability, be devoted to reduce cost always.The tool palette of these types also is widely used in many other industrial application, comprises the member of producing by for example boring of various machine operations, milling and turning.Normally used tool palette is made by being selected from AA2000 series alloy, AA6000 series alloy or AA7000 series alloy.
For the alloy that is used for profiled sheeting, with favorable mechanical processibility bonded high-wearing feature be important performance.In typical tool palette deformation alloy, by obtaining this wear resistance with copper (for example in AA2000 series) or zinc (for example in AA7000 series) or magnesium and silicon (for example in the AA6000 series) alloying and linkage heat mechanical treatment.In these heat treatable alloy species, the typical way that obtains high rigidity is the precipitation-hardening by the coherence phase.It has been generally acknowledged that by for example nascent (primary) Si of thick relatively particle and non-coherence Mg
2The additional sclerosis of Si is inappropriate, because there is the relevant risk of eutectic melting at elevated temperatures.(Cu) the additional sclerosis of Si dispersoid can improve the quenching sensitive of alloy because it has been generally acknowledged that them for Fe, Mn by α-Al also to be not easy application.The quenching sensitive that improves is considered to disadvantageous character, particularly for the product that approaches specification.
Typically, utilize AA2000 and AA7000 alloy to obtain to be higher than the AA6000 hardness of alloy.Yet the shortcoming of AA2000 series is high copper content, and this makes this alloy expensive and very responsive to thermal treatment.In addition, high copper content also has disadvantageous effect to the weldability of alloy.Have similar arguement for AA7000 series, for example high unrelieved stress and bad weldability and corrosive nature, this can make tolerance of dimension, repairing weldability and the weather resistance of model complicated.Usually, the AA6000 series alloy of T6 state for example the wear resistance of AA6010, AA6013, AA6061, AA6066, AA6070 and AA6082 be enough for common industrial application.Yet, for high performance application, needing higher wear resistance, can not have a negative impact simultaneously to weldability and cost.
The profiled sheeting that the purpose of this invention is to provide aluminium deformation alloy with improved wear.
According to the present invention, realized this purpose by the profiled sheeting that the aluminium deformation alloy that comprises following composition is provided, by weight percentage:
-Si 1.4-2.1
-Mn 0.8-1.2
-Cu 0.45-0.9
-Mg 0.7-1.2
-Ti ＜0.15
-Zn ＜0.4
-Fe ＜0.7
Among-Zr, Cr, the V one or more, every kind＜0.25, total amount is preferably＜0.35
-accidental element and impurity, every kind＜0.05, total amount＜0.25,
-surplus is an aluminium, and this profiled sheeting has the thickness greater than 0.6mm, and has the hardness that is higher than 105HB under the T6 state.
By the hardness that obtains in conjunction with Mg-Si-Cu phase, the precipitation-hardening (known these can by them to the age hardening effect in the actual minimizing of the influence of quenching sensitive balance AlMgSi (Cu) alloy) that contains Fe and contain intermetallic compound and the dispersoid of Mn and high excessive Si (this can reduce the Mg solute level and contain the negative impact of Mg dispersoid to quenching sensitive to minimize) to improve.The supersaturation level of Mg-Si phase is not high enough to make that extra high quenching sensitive is to be caused by Mg, Si and Cu solutes content.Think that balance alloy composition according to the present invention combines the intensity raising effect of silicon interpolation and amount of copper, magnesium and manganese.Find that this alloy provides gratifying weldability and the hardness of 105HB at least.It should be noted that hardness value is represented with the Brinell scale, and recorded by the ball with 2.5mm diameter that is loaded with the 62.5kg quality.Carry out hardness test according to ASTME10 (2002 editions).
In a preferred embodiment of the invention, the hardness of T6 state is 115HB, more preferably 120HB at least at least.These hardness values mean the machinability and the wear resistance of raising.Guarantee enough weldabilities and keep repairability thus with the chemical constitution of combined with heat treatment: surprisingly, have been found that Cu level for as many as 0.9%, use for example common 4043 filler wires (filler wire), the plate alloy demonstrates extraordinary repairability.
In one embodiment, Si is in the 1.53-2.0% scope, more preferably in the 1.55-1.9% scope.Find by coherence Mg-Si-Cu mutually and primary silicon, non-coherence Mg2Si and α-Al (Fe, Mn, the Cu) sclerosis of Si intermetallic compound phase and dispersoid, this silicon scope provides the combination of extraordinary desired properties.
In one embodiment, Mn is in the 0.85-1.10% scope.It is found that particularly by promote α-Al (Fe, Mn, Cu) the Si intermetallic compound mutually and the formation of dispersoid, this manganese scope provides the combination of extraordinary desired properties.Under high Si level, the trend that forms crisp relatively β-AlFeSi intermetallic compound phase increases.Yet, can stablize more favourable α-Al (Fe, Mn, Cu) Si phase by guaranteeing the existence of an amount of Mn and Cu.
In one embodiment, Cu is in the 0.5-0.7% scope.Find by coherence Mg-Si-Cu mutually and stable α-Al (Fe, Mn, Cu) Si, this copper scope provides the combination of extraordinary desired properties, keeps cost of alloy decline simultaneously and guarantees good repairing weldability.
In one embodiment, Zn is lower than 0.3%, preferably in the 0.17-0.3% scope.
In one embodiment, Fe preferably be at least 0.2%, more preferably the 0.2-0.5% scope and even more preferably in the 0.3-0.5% scope with α-Al (Fe, Mn, Cu) the Si intermetallic compound of the raising hardness of guaranteeing to form q.s.
In one embodiment, Zr, Cr, V each preferably be lower than 0.18%, more preferably less than 0.12% with further reduction quenching sensitive.
In one embodiment, profiled sheeting has " B " level or the better machinability grade that " ASM Specialty Handbook-Aluminium and Aluminium Alloys (J.R.Davis edits); ASMinternational 1993,328-331 page or leaf " limits.
In one embodiment, profiled sheeting has the final thickness of 300mm, wherein the hardness value that still meets the demands at this plate center.Preferably, final thickness is in the 5-300mm scope, more preferably in the 5-260mm scope.These thickness ranges allow profiled sheeting to be used for the practical application that all relate to profiled sheeting.
In one embodiment, only profiled sheeting is rolled down to final thickness by hot rolling.
According to a further aspect in the invention, provide the method that is prepared into template, this method may further comprise the steps:
Casting has the ingot casting of following composition, and this composition comprises (by weight percentage):
-Si 1.4-2.1
-Mn 0.8-1.2
-Cu 0.45-0.9
-Mg 0.7-1.2
-Ti ＜0.15
-Zn ＜0.4
-Fe ＜0.7
Among-Zr, Cr, the V one or more, every kind＜0.25, total amount is preferably＜0.35
-accidental element and impurity, every kind＜0.05, total amount＜0.25, surplus is an aluminium, and has the preferred compositing range of mentioning in the above description.
Homogenizing and/or preheating ingot casting,
Process described plate to final thickness, have preferred by hot rolling and/or cold rolling, more preferably only by hot rolling,
Comprise solution heat treatment refrigerative thermal treatment fast subsequently,
Timeliness,
Wherein select rate of cooling in the described quick process of cooling to obtain the profiled sheeting hardness of 105HB at least.
By making, obtain high rigidity product with high chip breaking (chip-breaking) intermetallic compound content according to profiled sheeting of the present invention.Rate of cooling in the quick process of cooling after solution heat treatment is important, because this rate of cooling has determined the solutes content of dissolved Mg, Si and Cu in the solution heat treatment process.
In one embodiment of the invention, the thermal treatment after hot rolling or the hot pressing is that T6 handles.
In one embodiment, homogenization temperature is at least 450 ℃, preferably at least 500 ℃, more preferably 500-595 ℃, preferred 1-25 hour, more preferably 10-16 hour.Preheating temperature is at least 570 ℃, between about 300-570 ℃, preferably between 350-530 ℃, and preferred 1-25 hour, more preferably 1-10 hour.
In one embodiment, solution heat treatment temperature is at least 500 ℃, preferably at least 520 ℃ and more preferably at least 540 ℃.In one embodiment, after solution heat treatment, be cooled to be lower than 250 ℃, preferably be lower than 150 ℃ and be at least 1 ℃/s, preferably at least 2 ℃/s more preferably 5 ℃/s even more preferably at least 10 ℃/s more preferably less than 100 ℃ rate of cooling from solution heat treatment temperature.It should be noted that the rate of cooling of product depends on the position in the product in the quenching process.The cooling of product center is slower than the surface of product.Therefore, because final hardness depends on rate of cooling, if local rate of cooling is lower in the quenching process, hardness will be lower so.Stagnation point in the product is defined as the minimum point of rate of cooling in the quenching process.Above-mentioned rate of cooling is relevant with the rate of cooling of stagnation point place.
In another embodiment, ag(e)ing process comprise continue maximum 28 days, preferably continue maximum 14 days, more preferably continue maximum 7 days, more preferably continue maximum 2 days natural aging, then be equivalent in about 1-10 hour artificial aging of about 180-200 ℃ timeliness and handle.It is known to those skilled in the art that the common not time and the temperature of independent selective annealing.Ag(e)ing process is heat activated, and this causes being equivalent to lesser temps and long period with short period of time bonded high temperature, promptly reaches identical metallurgy state after ageing treatment.
In one embodiment of the invention, procedure of processing comprises rolling or pressing step.In another embodiment, rolling step comprises hot rolling and/or heat-press step and/or cold rolling step.Preferably, procedure of processing only comprises hot rolling and/or hot pressing.
In one embodiment of the invention, the casting step is the casting step near net shape, and wherein the size of cast article approaches the finished product.
To explain specific embodiments of the present invention by following non-limiting example and accompanying drawing.It should be noted, change the chemical constitution of alloy by the smear metal (cutting) that mixes brazing alloy, thereafter can add Cu and/or Mg and/or other element obtaining final chemical constitution, this brazing alloy is that the AA3000 series core alloy of AA4000 series alloy of the rich Si of Al 99.0 constitutes by being coated with technical purity mainly.
The average composition of table 1. beta alloy and in the hardness of T6 state
| Alloy | Si | Fe | Cu | Mn | Mg | Zn | Ti | HB | Brazing alloy content (%) |
| Al99.0 | 0.4 | 0.6 | 0.03 | 0.03 | 0.03 | 0.07 | - | - | 0 |
| Brazing alloy | 2.0 | 0.4 | 0.5 | 1.0 | 0.40 | 0.25 | 0.05 | - | 100 |
| Embodiment 1 | 1.72 | 0.37 | 0.61 | 0.77 | 0.97 | 0.21 | 0.05 | 124 | 82 |
| Embodiment 2 | 1.70 | 0.39 | 0.91 | 0.95 | 0.85 | 0.21 | 0.05 | 124 | 81 |
| Example 3 | 2.10 | 0.38 | 0.50 | 1.03 | 0.88 | 0.25 | 0.05 | 124 | 100 |
| Embodiment 4 | 1.68 | 0.41 | 0.40 | 0.78 | 0.98 | 0.21 | 0.05 | 123 | 80 |
| Embodiment 5 | 1.71 | 0.43 | 0.51 | 0.76 | 0.70 | 0.21 | 0.05 | 122 | 82 |
| Embodiment 6 | 1.59 | 0.38 | 0.61 | 0.81 | 0.98 | 0.10 | 0.03 | 123 | 75 |
| Embodiment 7 | 1.60 | 0.39 | 0.64 | 0.95 | 0.91 | 0.02 | 0.05 | Fig. 1 | 80 |
In the temperature that is higher than 510 ℃ these alloys are carried out homogenizing, optionally carry out hot rolling, carry out solution heat treatment at 550 ℃, cool off so that the solutes content maximization of Mg, Si and Cu with at least 10 ℃/s, at room temperature store 14 days, and after the ageing treatment that is equivalent to 190 ℃ of lasting 2-6 hours, carry out timeliness.By this way, the high rigidity T6 state product that acquisition has high chip breaking intermetallic compound content causes the hardness of 120HB at least.Under 530 ℃ embodiment 7 is carried out solution heat treatment, at room temperature store 1 day, other treatment condition are with above given to other alloy.
Shown among Fig. 1 have 80,100 or 150mm thickness have a Hardness Distribution (profile) according to the plate of the composition of embodiment 7.Provide the distance (L) that arrives the plate center on the thickness direction of representing with mm along X-axis, and provide the hardness with the HB value representation of plate thickness different positions along Y-axis.Each position on all observed value display panel thickness has the hardness value of 120HB at least.
Should be understood that the present invention is not restricted to described embodiment and the above embodiments, but comprise any and all embodiments in specification sheets and the following claim scope.
Claims (13)
1. the profiled sheeting of aluminium deformation alloy, this profiled sheeting comprises by weight percentage:
-Si 1.4-2.1
-Mn 0.8-1.2
-Cu 0.45-0.9
-Mg 0.7-1.2
-Ti ＜0.15
-Zn ＜0.4
-Fe ＜0.7
Among-Zr, Cr, the V one or more, every kind＜0.25
-accidental element and impurity, every kind＜0.05, total amount＜0.25,
-surplus is an aluminium, and this profiled sheeting has the final thickness of 5-300mm, and has the hardness that is higher than 105HB at the T6 conditions.
2. according to the profiled sheeting of claim 1, wherein Si is in the 1.53-2.0% scope.
3. according to the profiled sheeting of claim 1 or 2, wherein Si is in the 1.55-1.9% scope.
4. according to the profiled sheeting of claim 1 or 2, wherein Mn is in the 0.85-1.10% scope.
5. according to the profiled sheeting of claim 1 or 2, wherein Cu is in the 0.5-0.7% scope.
6. according to the profiled sheeting of claim 1 or 2, wherein Mg is in the 0.9-1.1% scope.
7. according to the profiled sheeting of claim 1 or 2, wherein Zn is lower than 0.3%.
8. according to the profiled sheeting of claim 1 or 2, wherein Zn is in the 0.17-0.3% scope.
9. according to the profiled sheeting of claim 1 or 2, wherein profiled sheeting has " B " level or better machinability grade.
10. according to the profiled sheeting of claim 1 or 2, wherein profiled sheeting has the final thickness of 5-260mm scope.
11. the profiled sheeting according to claim 1 or 2 wherein only is rolled down to final thickness by hot rolling with profiled sheeting.
12. manufacture the method for template, may further comprise the steps:
Casting comprises the composition of following composition, by weight percentage:
-Si 1.4-2.1
-Mn 0.8-1.2
-Cu 0.45-0.9
-Mg 0.7-1.2
-Ti ＜0.15
-Zn ＜0.4
-Fe ＜0.7
Among-Zr, Cr, the V one or more, every kind＜0.25
-accidental element and impurity, every kind＜0.05, total amount＜0.25, surplus is an aluminium
Homogenizing and/or preheating,
Process the final thickness of described plate to 5-300mm,
Comprise solution heat treatment and be cooled fast to the rate of cooling of at least 1 ℃/s subsequently being lower than 250 ℃ thermal treatment,
Timeliness,
Wherein select rate of cooling in the described quick cooling to obtain the profiled sheeting hardness of 105HB at least.
13. according to the method for claim 12, wherein the thermal treatment of being undertaken after the processing of plate and hot rolling or the hot pressing by hot rolling or hot pressing is that T6 handles.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP04077718.7 | 2004-10-05 | ||
| EP04077718 | 2004-10-05 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101035919A CN101035919A (en) | 2007-09-12 |
| CN100562595C true CN100562595C (en) | 2009-11-25 |
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| Application Number | Title | Priority Date | Filing Date |
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| CNB2005800339626A Expired - Fee Related CN100562595C (en) | 2004-10-05 | 2005-10-04 | High hardness aluminium profiled sheeting and the method for producing described plate |
Country Status (9)
| Country | Link |
|---|---|
| US (1) | US20060070686A1 (en) |
| EP (1) | EP1802782B1 (en) |
| CN (1) | CN100562595C (en) |
| AT (1) | ATE389736T1 (en) |
| CA (1) | CA2582249A1 (en) |
| DE (2) | DE102005047406A1 (en) |
| ES (1) | ES2302247T3 (en) |
| FR (1) | FR2876117B1 (en) |
| WO (1) | WO2006037647A1 (en) |
Families Citing this family (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102006039684B4 (en) * | 2006-08-24 | 2008-08-07 | Audi Ag | Aluminum safety component |
| US9314826B2 (en) | 2009-01-16 | 2016-04-19 | Aleris Rolled Products Germany Gmbh | Method for the manufacture of an aluminium alloy plate product having low levels of residual stress |
| EP2379765B2 (en) * | 2009-01-16 | 2016-10-12 | Aleris Rolled Products Germany GmbH | Method for the manufacture of an aluminium alloy plate product having low levels of residual stress |
| US8613991B2 (en) * | 2009-10-08 | 2013-12-24 | Aleris Aluminum Duffel Bvba | Multilayer tube with an aluminum alloy core tube |
| JP5495183B2 (en) * | 2010-03-15 | 2014-05-21 | 日産自動車株式会社 | Aluminum alloy and high strength bolt made of aluminum alloy |
| MX2018008367A (en) * | 2016-01-08 | 2018-12-10 | Arconic Inc | New 6xxx aluminum alloys, and methods of making the same. |
| SI24911A (en) | 2016-03-04 | 2016-07-29 | Impol 2000, d.d. | High-strength aluminum alloy Al-Mg-Si and procedure for its manufacture |
| CN107245614B (en) * | 2017-07-27 | 2019-01-22 | 广州致远新材料科技有限公司 | A kind of wear-resistant aluminum alloy and application thereof |
| CN108300907B (en) * | 2018-02-10 | 2020-07-21 | 沈阳航空航天大学 | Al-Mn-Si-Mg alloy material and preparation method thereof |
| CN109136670B (en) * | 2018-08-21 | 2019-11-26 | 中南大学 | A kind of 6XXX line aluminium alloy and preparation method thereof |
| CN112430766B (en) * | 2020-11-03 | 2022-02-18 | 福建祥鑫股份有限公司 | High-strength low-yield-ratio 6-series aluminum alloy and preparation method thereof |
| JP2022150384A (en) * | 2021-03-26 | 2022-10-07 | 本田技研工業株式会社 | Aluminum alloy, manufacturing method for additive-manufactured article, and additive-manufactured article |
| CN114277268B (en) * | 2021-12-24 | 2023-04-07 | 东北轻合金有限责任公司 | Manufacturing method of aluminum alloy foil for brazing |
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| EP0786535A1 (en) * | 1994-02-16 | 1997-07-30 | Sumitomo Light Metal Industries, Ltd. | Method of manufacturing aluminum alloy plate for molding |
| US5858134A (en) * | 1994-10-25 | 1999-01-12 | Pechiney Rhenalu | Process for producing alsimgcu alloy products with improved resistance to intercrystalline corrosion |
| US5961752A (en) * | 1994-04-07 | 1999-10-05 | Northwest Aluminum Company | High strength Mg-Si type aluminum alloy |
| JP2001162318A (en) * | 1999-08-25 | 2001-06-19 | Furukawa Electric Co Ltd:The | Aluminum alloy for forming to automotive member, method for producing same alloy material and automotive member for forming |
| EP1167560A1 (en) * | 2000-06-27 | 2002-01-02 | Corus Aluminium Voerde GmbH | Aluminium casting alloy |
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|---|---|---|---|---|
| JPH04325650A (en) * | 1991-04-24 | 1992-11-16 | Kobe Steel Ltd | Aluminum alloy for metal mold and its production |
| JPH04325645A (en) * | 1991-04-25 | 1992-11-16 | Furukawa Alum Co Ltd | Aluminum alloy excellent in strength after baking hardening and its production |
| JPH07197219A (en) * | 1993-12-28 | 1995-08-01 | Furukawa Electric Co Ltd:The | Production of aluminum alloy sheet for forming |
| US6004409A (en) * | 1997-01-24 | 1999-12-21 | Kaiser Aluminum & Chemical Corporation | Production of high quality machinable tolling plate using brazing sheet scrap |
| FR2807449B1 (en) * | 2000-04-07 | 2002-10-18 | Pechiney Rhenalu | METHOD FOR MANUFACTURING STRUCTURAL ELEMENTS OF ALUMINUM ALLOY AIRCRAFT AL-SI-MG |
-
2005
- 2005-10-03 US US11/240,629 patent/US20060070686A1/en not_active Abandoned
- 2005-10-04 WO PCT/EP2005/010805 patent/WO2006037647A1/en active IP Right Grant
- 2005-10-04 AT AT05805867T patent/ATE389736T1/en not_active IP Right Cessation
- 2005-10-04 ES ES05805867T patent/ES2302247T3/en active Active
- 2005-10-04 CA CA002582249A patent/CA2582249A1/en not_active Abandoned
- 2005-10-04 DE DE102005047406A patent/DE102005047406A1/en not_active Ceased
- 2005-10-04 FR FR0510136A patent/FR2876117B1/en not_active Expired - Fee Related
- 2005-10-04 EP EP05805867A patent/EP1802782B1/en active Active
- 2005-10-04 DE DE602005005509T patent/DE602005005509T2/en not_active Expired - Fee Related
- 2005-10-04 CN CNB2005800339626A patent/CN100562595C/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0786535A1 (en) * | 1994-02-16 | 1997-07-30 | Sumitomo Light Metal Industries, Ltd. | Method of manufacturing aluminum alloy plate for molding |
| US5961752A (en) * | 1994-04-07 | 1999-10-05 | Northwest Aluminum Company | High strength Mg-Si type aluminum alloy |
| US5858134A (en) * | 1994-10-25 | 1999-01-12 | Pechiney Rhenalu | Process for producing alsimgcu alloy products with improved resistance to intercrystalline corrosion |
| JP2001162318A (en) * | 1999-08-25 | 2001-06-19 | Furukawa Electric Co Ltd:The | Aluminum alloy for forming to automotive member, method for producing same alloy material and automotive member for forming |
| EP1167560A1 (en) * | 2000-06-27 | 2002-01-02 | Corus Aluminium Voerde GmbH | Aluminium casting alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| EP1802782A1 (en) | 2007-07-04 |
| DE602005005509D1 (en) | 2008-04-30 |
| US20060070686A1 (en) | 2006-04-06 |
| WO2006037647A1 (en) | 2006-04-13 |
| ATE389736T1 (en) | 2008-04-15 |
| ES2302247T3 (en) | 2008-07-01 |
| DE602005005509T2 (en) | 2009-04-16 |
| FR2876117A1 (en) | 2006-04-07 |
| EP1802782B1 (en) | 2008-03-19 |
| DE102005047406A1 (en) | 2006-06-01 |
| CN101035919A (en) | 2007-09-12 |
| CA2582249A1 (en) | 2006-04-13 |
| FR2876117B1 (en) | 2007-10-26 |
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