KR20100018048A - A structural material part of a high-si mg-containing al alloy and the manufacture method thereof - Google Patents
A structural material part of a high-si mg-containing al alloy and the manufacture method thereof Download PDFInfo
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Abstract
Description
본 발명은 알루미늄 합금과 그 제조기술에 관한 것으로, 특히 마그네슘을 함유한 고 규소 알루미늄 합금 및 그 제조방법에 관한 것이다. TECHNICAL FIELD This invention relates to aluminum alloys and its manufacturing technique. Specifically, It is related with the high silicon aluminum alloy containing magnesium, and its manufacturing method.
알루미늄 규소 합금(Aluminium-silicon alloy), 특히 고 규소 함량의 알루미늄 규소합금은 저밀도, 높은 내마모성, 높은 항 부식성과 낮은 열팽창 계수를 가지고 있어 자동차 산업과 항공 산업에서 광범위하게 응용된다. 그러나 보통의 응고방법으로 제작된 알루미늄 규소 합금은 그 초기형태 중에 큰 괴상을 해소하기 힘들기에 먼저 규소(Si) 입자와 판 가닥 모양의 공융(eutectic)조직이 석출함으로 하여 합금의 강도가 떨어지고 취약성이 높아져 가소성 가공을 거쳐 응고조직을 개선하여 각종 단면형태의 고성능재료를 제조하기 힘들뿐만 아니라 응고조직의 개선과 각종 단면모양의 고성능 재료를 가공하기 어렵고 합금의 응용범위를 제한하게 된다. 전통적으로 알루미늄 규소합금은 변형능력이 취약하여 주조 알루미늄 합금에 귀속시킨다. 취약한 변형능력을 개선하기 위해서 쾌속 응고의 방법을 모색해 왔으나 오직 크기가 작은(<10mm)것만 얻게 되고 치수가 큰 부품을 제조하려면 연속공정이 있어야 했다. 대표적인 예를 들면 분말야금의 방법을 통해 제조하는 것인데 그 생산비용이 높으며 프로세스는 매우 복잡하다. Aluminum-silicon alloys, especially aluminum alloys of high silicon content, have low density, high wear resistance, high corrosion resistance and low coefficient of thermal expansion, making them widely used in the automotive and aviation industries. However, the aluminum silicon alloy produced by the normal solidification method is difficult to resolve the large mass in its initial form, so the silicon (Si) particles and the plate-like eutectic structure are precipitated first, so the strength of the alloy decreases and the fragility is weak. It is difficult to manufacture high-performance materials of various cross-sections by improving the solidification structure through plastic processing, and it is difficult to improve the solidification structure and process high-performance materials of various cross-sections and limit the application range of the alloy. Traditionally, aluminum silicon alloys are weakly deformable and are attributed to cast aluminum alloys. Rapid solidification methods have been sought to improve fragile deformation, but only small (<10mm) sizes have been obtained, and manufacturing a large dimension required a continuous process. A typical example is the production of powder metallurgy, which has a high production cost and a very complicated process.
산업용 순 알루미늄과 알루미늄 합금의 생산에서 반연속 주조방법(Direct Chill Casting, 약칭하여 DC주조)은 줄곧 광범위하게 사용되어 왔는데, 주로 어떻게 합금의 성분편차를 감소하는가와 결정입자의 크기를 줄이는 것 그리고 표면품질을 제고하는데 주의를 돌리고 있다. 반연속 주조방법을 이용해 큰 크기의 규격을 가지고 어떠한 개질제(예를 들어 P, Na, Sr 등)도 함유하지 않은 고 규소 알루미늄 합금을 제조하는 기술은 이미 본 발명의 발명자 중의 한 사람이 특허문헌 1로 중국특허를 받았다. In the production of industrial pure aluminum and aluminum alloys, semi-continuous casting (DC casting) has been widely used all the time, mainly how to reduce the constituent deviations of the alloys and to reduce the grain size and surface. Attention has been paid to improving quality. The technique for producing a high silicon aluminum alloy having a large size using a semi-continuous casting method and containing no modifier (for example, P, Na, Sr, etc.) has already been made by one of the inventors of the present invention. Received a Chinese patent.
발명자의 진일보한 연구를 통해 상술한 발명기술을 이용하여 Si의 하한 함량(8%중량)을 증가시키고 Si의 상한함량(18%중량)을 저하시키며, Mg의 함량과 기타 함금원소의 함량을 조정하여 열가소성 공정과 연속 열처리를 통해 양호한 가소성을 구비하고 고강도의 마그네슘을 함유한 고 규소 알루미늄 합금을 제조하게 된다.The inventors have made further research to increase the lower limit content (8% weight) of Si, lower the upper limit content of Si (18% weight), and adjust the content of Mg and other alloying elements by using the above-described invention technology. Through the thermoplastic process and the continuous heat treatment to produce a high silicon aluminum alloy having good plasticity and containing high strength magnesium.
본 발명의 목적은 마그네슘을 함유한 고 규소 알루미늄 합금 및 그 제조방법으로서 주조과정에서 어떠한 개질제(modifier)도 첨가하지 않고, 열가소성 공정과 열처리를 통해 저비용으로 양호한 가소성과 고강도를 가진 마그네슘을 함유한 고 규소 알루미늄 합금을 제조하는데 있다. An object of the present invention is a high silicon aluminum alloy containing magnesium, and a method for producing the same, which does not add any modifier in the casting process, and contains magnesium having good plasticity and high strength at low cost through a thermoplastic process and heat treatment. To produce a silicon aluminum alloy.
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법은 형재, 봉재, 판재와 단조재를 포함하는 마그네슘을 함유한 고 규소 알루미늄 합금의 잉곳(ingot)을 반연속 주조방법으로 주조하는 제1단계와; 공융 규소입자를 분산하기 위해 예열처리하는 제2단계; 및 상기 알루미늄 합금을 최종형태 및 개질된 마이크로조직(microstructure)으로 만들기 위해 열가소성 공정 및 열처리를 하는 제3단계를 포함하며, 상기 단계에 의해 제조된 알루미늄 합금은 알루미늄 본체의 결정립 미세화 강화, 규소입자의 분산강화, 제2상 입자의 침전강화에 의해 강화되고, 마그네슘 함량은 0.2-2.0wt%이고. 규소 함량은 8-18wt%이고, 균질하고 미세한 마이크로조직을 가지며, 평균 결정립 크기가 <6㎛인 등방성(exquiaxed) 입자이고, 규소(Si)와 제2상 입자는 평균 결정립 크기가 <5㎛로 분산되는 것을 특징으로 한다. The method for producing a high silicon aluminum alloy containing magnesium of the present invention is a first step of casting an ingot of a high silicon aluminum alloy containing magnesium, including a mold, a bar, a plate, and a forging by a semi-continuous casting method. Wow; Preheating to disperse the eutectic silicon particles; And a third step of performing a thermoplastic process and heat treatment to make the aluminum alloy into a final form and a modified microstructure, wherein the aluminum alloy prepared by the step is a reinforcing grain refinement of the aluminum body, Strengthened by dispersion strengthening, precipitation strengthening of the second phase particles, magnesium content is 0.2-2.0wt%. Silicon content is 8-18wt%, homogeneous and fine microstructure, isotropic (exquiaxed) particles with an average grain size of <6 μm, and silicon (Si) and second phase particles with an average grain size of <5 μm It is characterized by being dispersed.
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법에 있어서, 상기 알루미늄 합금은 적어도 하나의 Cu, Zn, Ni, Ti, Fe 중 적어도 하나를 포함하며, 총 함량은 2wt%와 같거나 2wt%보다 낮은 것을 특징으로 한다. In the method for producing a magnesium-containing high silicon aluminum alloy of the present invention, the aluminum alloy comprises at least one of Cu, Zn, Ni, Ti, Fe, the total content is equal to or 2wt% It is characterized by being lower.
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법에 있어서, 제1단계의 반연속 주조방법의 주조온도는 알루미늄 합금의 액상선 이상의 150-300℃이고, 주조속도는 100-200㎜/min이고, 알루미늄 합금의 잉곳 주변의 냉각수량은 5-15g/㎜ㆍs이며, 반연속 주조방법에는 개질제가 첨가되지 않으며, 제2단계에서 알루미늄 합금의 잉곳은 가열속도 10-30℃/min, 가열온도 450-520℃, 유지시간 1-3시간에서 공융 규소입자를 분산하기 위해 예열되며, 제3단계에서 알루미늄 합금은 400-520℃에서 고온 변형되고, 이후 자연냉각 또는 강제냉각되며, 열가소성 공정 이후 열처리 되는 것을 특징으로 한다. In the manufacturing method of the high silicon aluminum alloy containing magnesium of the present invention, the casting temperature of the semi-continuous casting method of the first step is 150-300 ℃ above the liquidus line of the aluminum alloy, the casting speed is 100-200 mm / min The amount of cooling water around the ingot of the aluminum alloy is 5-15 g / mm · s, the modifier is not added in the semi-continuous casting method, and in the second step, the ingot of the aluminum alloy is heated at a heating rate of 10-30 ° C./min, and heated. Preheated to disperse eutectic silicon particles at a temperature of 450-520 ° C and a holding time of 1-3 hours, in the third step, the aluminum alloy is deformed at 400-520 ° C at high temperature, after which it is naturally cooled or forced-cooled, and after the thermoplastic process It is characterized in that the heat treatment.
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법에 있어서,제3단계는 자연냉각으로 열가소성 공정을 거친 후의 알루미늄 합금은 고용처리 단계와 인공시효처리 단계를 포함하는데, 고용처리시의 가열속도는 10-30℃/min이고, 고용처리온도는 500-540℃이고, 고용처리시간은 0.5-3시간이며, 인공시효처리시의 시효온도는 160-200℃이고, 시효시간은 1-10시간인 것을 특징으로 한다. In the method for producing a high silicon aluminum alloy containing magnesium of the present invention, the third step is the aluminum alloy after the thermoplastic process by natural cooling comprises a solid solution treatment step and an artificial aging treatment step, the heating rate during the solid solution treatment Is 10-30 ℃ / min, solid solution treatment temperature is 500-540 ℃, solid solution treatment time is 0.5-3 hours, aging temperature in artificial aging treatment is 160-200 ℃, and aging time is 1-10 hours. It is characterized by that.
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법에 있어서,제3단계는 열가소성 공정후 알루미늄 합금을 강제냉각하기 위해서 인공시효 또는 자연시효처리 단계를 포함하는데, 인공시효처리시의 시효온도는 160-200℃이고, 시효시간은 1-10시간인 것을 특징으로 한다. In the manufacturing method of the high silicon aluminum alloy containing magnesium of the present invention, the third step includes an artificial aging or natural aging treatment step for forced cooling of the aluminum alloy after the thermoplastic process, the aging temperature during the artificial aging treatment is 160-200 ℃, the aging time is characterized in that 1-10 hours.
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법에 있어서,제3단계의 열가소성 공정에서 열간압연(hot rolling) 단계를 포함하는데, 열간압연의 총 저감량(total reduction amount)은 40%보다 더 큰 것을 특징으로 한다. In the manufacturing method of the high silicon aluminum alloy containing magnesium of the present invention, it includes a hot rolling step in the thermoplastic process of the third step, the total reduction amount of the hot rolling is more than 40% It is characterized by large.
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법에 있어서, 제3단계의 열가소성 공정에서 열간압출(hot extrusion) 단계를 포함하는데, 열간압출의 압출비는 15보다 더 큰 것을 특징으로 한다. In the method for producing a magnesium-containing high silicon aluminum alloy of the present invention, the method includes a hot extrusion step in the thermoplastic process of the third step, wherein the extrusion ratio of the hot extrusion is greater than 15.
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법에 있어서, 제3단계의 열가소성 공정에서 열간단조(hot forging) 단계를 포함하는데, 열간단조의 단조비는 40%보다 더 큰 것을 특징으로 한다. In the method for producing a magnesium-containing high silicon aluminum alloy of the present invention, the method includes a hot forging step in the thermoplastic process of the third step, wherein the forging ratio of the hot forging is greater than 40%. .
본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금 및 그 제조방법은 주조단계에서 어떠한 개질제도 첨가하지 않은 상태에서 반연속 주조방법으로 열가소성 가공과 열처리를 거쳐 저비용으로 양호한 가소성과 비교적 고강도를 가진 구조재로 이용가능한 마그네슘을 함유한 고 규소 알루미늄 합금이 제조된다. The high silicon aluminum alloy containing magnesium of the present invention and its manufacturing method are semi-continuous casting methods without any modification agent in the casting step, and are used as structural materials having good plasticity and relatively high strength at low cost through thermoplastic processing and heat treatment. High silicon aluminum alloys containing as much magnesium as possible are produced.
도 1은 본 발명의 반연속 주조장치의 구조도.
도 2는 본 발명의 실시예 1에 따라 반연속 주조(주조온도는 730℃, 주조속도 180㎜/min, 냉각수량 8g/㎜ㆍs)로 주조된 Al-12.7Si-0.7Mg-0.3Fe 합금(#3)의 마이크로조직.
도 3은 본 발명의 실시예 1에 따라 반연속 주조(주조온도는 730℃, 주조속도 180㎜/min, 냉각수량 8g/㎜ㆍs)로 주조된 Al-12.7Si-0.7Mg-0.3Fe 합금(#3)의 고배율 마이크로조직.
도 4는 본 발명의 실시예 2에 따라 2시간 동안 500℃ 예열처리, 470℃에서 열압출(압출비 15) 후의 Al-12.7Si-0.7Mg-0.3Fe 합금(#3)의 마이크로조직.
도 5는 본 발명의 실시예 3에 따라 2시간 동안 500℃ 예열처리, 470℃에서 열압출(압출비 15) 후의 Al-12.7Si-0.7Mg-0.3Fe 합금(#3)의 T6 상태(1시간 동안 고용온도 540℃, 3시간 동안 인공시효온도 200℃)의 마이크로조직.
도 6은 본 발명의 실시예 1에 따라 반연속 주조(주조온도는 800℃, 주조속도 140㎜/min, 냉각수량 10g/㎜ㆍs)로 주조된 Al-15.5Si-0.7Mg-0.72Fe 합금(#5)의 마이크로조직.
도 7은 본 발명의 실시예 1에 따라 반연속 주조(주조온도는 800℃, 주조속도 140㎜/min, 냉각수량 10g/㎜ㆍs)로 주조된 Al-15.5Si-0.7Mg-0.72Fe 합금(#5)의 고배율 마이크로조직.
도 8은 본 발명의 실시예 2에 따라 2시간 동안 500℃ 예열처리, 470℃에서 열압출(압출비 45) 후의 Al-15.5Si-0.7Mg-0.72Fe 합금(#5)의 마이크로조직.
도 9는 본 발명의 실시예 3에 따라 1시간 동안 500℃ 예열처리, 500℃에서 열압(압출량 60%) 후의 Al-15.5Si-0.7Mg-0.72Fe 합금(#5)의 마이크로조직.
도 10은 본 발명의 실시예 3에 따라 2시간 동안 500℃ 예열처리, 470℃에서 열압출(압출비 45) 후의 Al-15.5Si-0.7Mg-0.27Fe 합금(#5)의 T6 상태(2시간 동안 고용온도 520℃, 4시간 동안 인공시효온도 180℃)의 마이크로조직.
도 11은 본 발명의 실시예 3에 따라 1시간 동안 500℃ 예열처리, 500℃에서 열압(압출량 60%) 후의 Al-15.5Si-0.7Mg-0.27Fe 합금(#5)의 T6 상태(3시간 동안 고용온도 520℃, 4시간 동안 인공시효온도 200℃)의 마이크로조직.
도 12는 본 발명의 실시예 3에 따라 2시간 동안 500℃ 예열처리, 470℃에서 열압출(압출비 45) 후의 Al-15.5Si-0.7Mg-0.27Fe 합금(#5)의 T6 상태(2시간 동안 고용온도 520℃, 4시간 동안 인공시효온도 180℃)의 고배율 마이크로조직.
도 13은 본 발명의 실시예 1에 따라 반연속 주조(주조온도는 850℃, 주조속도 120㎜/min, 냉각수량 10g/㎜ㆍs)로 주조된 Al-17.5Si-0.7Mg-1.0Cu-0.72Fe 합금(#7)의 마이크로조직.1 is a structural diagram of a semi-continuous casting apparatus of the present invention.
Figure 2 is an Al-12.7Si-0.7Mg-0.3Fe alloy cast in semi-continuous casting (casting temperature is 730 ℃, casting speed 180mm / min, cooling water amount 8g / mm · s) according to Example 1 of the present invention Microstructure of (# 3).
Figure 3 is an Al-12.7Si-0.7Mg-0.3Fe alloy cast in semi-continuous casting (casting temperature is 730 ℃, casting speed 180mm / min, cooling water amount 8g / mm · s) according to Example 1 of the present invention High magnification microstructure of (# 3).
4 is a microstructure of Al-12.7Si-0.7Mg-0.3Fe alloy (# 3) after heat pretreatment at 500 ° C. for 2 hours and heat extrusion at 470 ° C. (extrusion ratio 15) according to Example 2 of the present invention.
5 is a T6 state (1) of Al-12.7Si-0.7Mg-0.3Fe alloy (# 3) after preheating at 500 ° C. for 2 hours and thermal extrusion at 470 ° C. (extrusion ratio 15) according to Example 3 of the present invention. Microstructure of solid solution temperature 540 ℃ for 3 hours, artificial aging temperature 200 ℃ for 3 hours.
6 is an Al-15.5Si-0.7Mg-0.72Fe alloy cast in semi-continuous casting (casting temperature is 800 ° C., casting speed 140 mm / min, cooling water amount 10 g / mm · s) according to Example 1 of the present invention. Microstructure of (# 5).
7 is an Al-15.5Si-0.7Mg-0.72Fe alloy cast in semi-continuous casting (casting temperature is 800 ° C., casting speed 140 mm / min, cooling water amount 10 g / mm · s) according to Example 1 of the present invention. High magnification microstructure of (# 5).
8 is a microstructure of Al-15.5Si-0.7Mg-0.72Fe alloy (# 5) after heat pretreatment at 500 ° C. for 2 hours and heat extrusion (extrusion ratio 45) at 470 ° C. according to Example 2 of the present invention.
FIG. 9 is a microstructure of Al-15.5Si-0.7Mg-0.72Fe alloy (# 5) after 500 ° C preheating for 1 hour and thermal pressure (extrusion amount 60%) at 500 ° C according to Example 3 of the present invention.
10 is a T6 state of Al-15.5Si-0.7Mg-0.27Fe alloy (# 5) after heat pretreatment at 500 ° C. for 2 hours and heat extrusion at 470 ° C. (extrusion ratio 45) according to Example 3 of the present invention. Microstructure of solid solution temperature 520 ℃ for 4 hours, artificial aging temperature 180 ℃ for 4 hours.
11 is a T6 state (3) of Al-15.5Si-0.7Mg-0.27Fe alloy (# 5) after 500 ° C preheating for 1 hour and thermal pressure (extrusion amount 60%) at 500 ° C according to Example 3 of the present invention. Microstructure of solid solution temperature 520 ℃ for 4 hours, artificial aging temperature 200 ℃ for 4 hours.
12 shows the T6 state of Al-15.5Si-0.7Mg-0.27Fe alloy (# 5) after heat pretreatment at 500 ° C. for 2 hours and heat extrusion at 470 ° C. (extrusion ratio 45) according to Example 3 of the present invention. High magnification microstructure of solid solution temperature 520 ℃ for 4 hours, artificial aging temperature 180 ℃ for 4 hours.
FIG. 13 shows Al-17.5Si-0.7Mg-1.0Cu- cast in semi-continuous casting (casting temperature is 850 ° C., casting speed 120 mm / min, cooling water amount 10 g / mm · s) according to Example 1 of the present invention. Microstructure of 0.72Fe Alloy (# 7).
본 발명의 관건은 전통적인 기술의 편견을 극복하고 어떠한 변질제도 첨가하지 않고 전통적인 반연속 주조방법을 이용하여 마그네슘을 함유한 고 규소 알루미늄 합금을 제조하였으며, 열가소성 공정과 열처리를 결합하여 생각지도 못한 기술효과를 가져오게 되였는데, 즉 미세하고 분산된 규소입자와 제2상 입자가 등방성 결정립 알루미늄 본체에 분포하여 양호한 가소성과 고강도의 신형 알루미늄 합금을 얻게 된다. The key point of the present invention is to overcome the bias of the traditional technology and to produce a high-silicon aluminum alloy containing magnesium by using the traditional semi-continuous casting method without adding any alteration agent, the unexpected technical effect by combining the thermoplastic process and heat treatment That is, the fine and dispersed silicon particles and the second phase particles are distributed in the isotropic grain aluminum body to obtain a new aluminum alloy of good plasticity and high strength.
표 1은 본 발명의 알루미늄 합금(Al-8.5Si-1.8Mg-0.2Fe, Al-12.7Si-0.7Mg-1.5Cu-0.3Ni-0.3Ti-0.4Fe, Al-15.5Si-0.7Mg-0.27Fe)과 T5과 T6 상태의 중국국가표준 6063 합금의 기계적 특성을 비교한 것이다. Table 1 shows the aluminum alloy of the present invention (Al-8.5Si-1.8Mg-0.2Fe, Al-12.7Si-0.7Mg-1.5Cu-0.3Ni-0.3Ti-0.4Fe, Al-15.5Si-0.7Mg-0.27Fe ) And mechanical properties of Chinese National Standard 6063 alloy in T5 and T6 state.
분명하게 Al-8.5Si-1.8Mg-0.2Fe, Al-12.7Si-0.7Mg-1.5Cu-0.3Ni-0.3Ti-0.4Fe와 Al-15.5Si-0.7Mg-0.27Fe 합금은 T6 상태의 항복강도와 인장강도는 모두 T6상태의 중국국가표준 6063 합금보다 높았다. T1 상태의 합금은 특히 연신율에 있어서 T5 상태의 중국국가표준 6063 합금보다 높았다. 6063 합금은 가장 통용되는 압출 형재 합금으로서 국내외에서 대량으로 건축, 차량, 장식 등 영역에서 사용되며 넓은 시장적 수요를 가지고 있다. 본 발명의 마그네슘을 함유한 고 규소 알루미늄 합금이 부분적으로 6063 합금을 대체하게 되면 반드시 거대한 경제적 이익을 가져오게 될 것이다. 게다가 알루미늄 합금에 규소 량을 증가시켜 사용함으로써 알루미늄 자원의 대량절약이 가능하다.
Clearly, Al-8.5Si-1.8Mg-0.2Fe, Al-12.7Si-0.7Mg-1.5Cu-0.3Ni-0.3Ti-0.4Fe and Al-15.5Si-0.7Mg-0.27Fe alloys have yield strength of T6. And tensile strength were both higher than T6 state standard 6063 alloy. The alloy in the T1 state was higher than the Chinese national standard 6063 alloy in the T5 state, especially in elongation. The 6063 alloy is the most commonly used extruded shape alloy, which is used in a large number of domestic and international construction, vehicles, and decoration areas, and has a wide market demand. The replacement of the 6063 alloy by the high silicon aluminum alloy containing magnesium of the present invention will necessarily bring huge economic benefits. In addition, by increasing the amount of silicon used in aluminum alloys, large amounts of aluminum resources can be saved.
<실시예 1> 반연속 주조 Example 1 Semi-Continuous Casting
반연속 주조를 위해 고안된 반연속 주조장치는 도 1과 같다. 도 1에서 1-냉각수 입구, 2-결정화기, 3-잉곳원료, 4-열정(hot top), 5-흑연링, 6-액체금속이다. 알루미늄 합금의 조성성분(wt%)은 표 2와 같고 파라미터는 표3과 같다.Semi-continuous casting device designed for semi-continuous casting is shown in FIG. In FIG. 1 there is a 1-cooled water inlet, 2-crystallizer, 3-ingot raw material, 4-hot top, 5-graphite ring, 6-liquid metal. The composition (wt%) of the aluminum alloy is shown in Table 2 and the parameters are shown in Table 3.
<실시예 2> 제2단계의 예열처리 후의 열간압출, 열간압연, 열간단조Example 2 Hot Extrusion, Hot Rolling, Hot Forging After Preheating Treatment of Second Step
제2단계의 예열처리에서 잉곳은 설정한 가열속도로 오븐에서 가열되어 설정온도에 도달한 후 잉곳은 설정시간 동안 유지된다. 이후 열간압출기, 열간압연기와 열간단조기를 사용하여 열가소성 공정을 완료한다.In the preheating process of the second stage, the ingot is heated in the oven at the set heating rate to reach the set temperature, and then the ingot is maintained for the set time. The thermoplastic process is then completed using a hot extruder, a hot mill and a hot forging machine.
표 4는 알루미늄 합금 각각의 예열 및 열간압출의 파라미터를 나타내고, 표 5는 알루미늄 합금 각각의 예열 및 열간압연의 파라미터를 나타내며, 표 6은 알루미늄 합금 각각의 예열 및 열간단조의 파라미터를 나타낸다.Table 4 shows the parameters of preheating and hot extrusion of each of the aluminum alloys, Table 5 shows the parameters of preheating and hot rolling of each of the aluminum alloys, and Table 6 shows the parameters of preheating and hot forging of each of the aluminum alloys.
<실시예 3> 열간압출, 열간압연, 열간단조의 열간변형 이후의 열처리<Example 3> Heat treatment after hot deformation of hot extrusion, hot rolling, hot forging
열간압출, 열간압연, 열간단조 이후 설정온도에서 잉곳이 열처리된다. After hot extrusion, hot rolling and hot forging, the ingot is heat treated at the set temperature.
표 7은 열간압출의 파라미터를 나타내고, 표 8은 열간압연의 파라미터를 나타내며, 표 9는 열간단조의 파라미터를 나타낸다. 표 10은 열처리 이후의 알루미늄 합금의 기계적 특성을 나타낸다. Table 7 shows the parameters of hot extrusion, Table 8 shows the parameters of hot rolling, and Table 9 shows the parameters of hot forging. Table 10 shows the mechanical properties of the aluminum alloy after heat treatment.
Claims (8)
상기 단계에 의해 제조된 알루미늄 합금은 알루미늄 본체의 결정립 미세화 강화, 규소입자의 분산강화, 제2상 입자의 침전강화에 의해 강화되고, 마그네슘 함량은 0.2-2.0wt%이고. 규소 함량은 8-18wt%이고, 균질하고 미세한 마이크로조직을 가지며, 평균 결정립 크기가 <6㎛인 등방성(exquiaxed) 입자이고, 규소(Si)와 제2상 입자는 평균 결정립 크기가 <5㎛로 분산되는 것을 특징으로 하는 마그네슘을 함유한 고 규소 알루미늄 합금의 제조방법.A first step of casting an ingot of a high silicon aluminum alloy containing magnesium including a mold, a bar, a plate, and a forging by a semi-continuous casting method; Preheating to disperse the eutectic silicon particles; And a third step of performing a thermoplastic process and heat treatment to make the aluminum alloy into a final form and a modified microstructure.
The aluminum alloy prepared by the above step is strengthened by strengthening grain refinement of the aluminum body, strengthening dispersion of silicon particles, and precipitation strengthening of the second phase particles, and magnesium content is 0.2-2.0 wt%. Silicon content is 8-18wt%, homogeneous and fine microstructure, isotropic (exquiaxed) particles with an average grain size of <6 μm, and silicon (Si) and second phase particles with an average grain size of <5 μm A method for producing a high silicon aluminum alloy containing magnesium, characterized in that dispersed.
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| CN1298878C (en) * | 2003-12-03 | 2007-02-07 | 东华大学 | Aluminum silicon alloy series possessing granulated silicon phase and its process |
| JP4474528B2 (en) * | 2004-11-01 | 2010-06-09 | 独立行政法人産業技術総合研究所 | Hyper-eutectic Al-Si alloy material with high toughness and forge forming |
| CN100392129C (en) * | 2004-11-18 | 2008-06-04 | 东北大学 | Large-sized hypereutectic high-seleium aluminium alloy billet and preparation method thereof |
| JP4773796B2 (en) * | 2005-10-28 | 2011-09-14 | 昭和電工株式会社 | Aluminum alloy continuous casting rod, continuous casting rod casting method, continuous casting equipment |
-
2008
- 2008-06-30 EP EP08772999.2A patent/EP2172572B1/en not_active Not-in-force
- 2008-06-30 KR KR1020107000263A patent/KR20100018048A/en not_active Application Discontinuation
- 2008-06-30 CN CN2008101376030A patent/CN101333614B/en not_active Expired - Fee Related
- 2008-06-30 JP JP2010513624A patent/JP2010531388A/en active Pending
- 2008-06-30 WO PCT/CN2008/001246 patent/WO2009003365A1/en active Application Filing
- 2008-06-30 CA CA002689332A patent/CA2689332A1/en not_active Abandoned
- 2008-06-30 RU RU2009149092/02A patent/RU2463371C2/en not_active IP Right Cessation
- 2008-06-30 US US12/451,232 patent/US20100126639A1/en not_active Abandoned
Also Published As
| Publication number | Publication date |
|---|---|
| EP2172572B1 (en) | 2013-05-15 |
| RU2463371C2 (en) | 2012-10-10 |
| EP2172572A4 (en) | 2010-12-15 |
| CN101333614B (en) | 2010-09-01 |
| CA2689332A1 (en) | 2009-01-08 |
| WO2009003365A1 (en) | 2009-01-08 |
| US20100126639A1 (en) | 2010-05-27 |
| EP2172572A1 (en) | 2010-04-07 |
| RU2009149092A (en) | 2011-08-10 |
| JP2010531388A (en) | 2010-09-24 |
| CN101333614A (en) | 2008-12-31 |
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