TW202010851A

TW202010851A - Aluminum magnesium alloy and method for producing the same

Info

Publication number: TW202010851A
Application number: TW107131757A
Authority: TW
Inventors: 丁仕旋; 石漢正; 庾忠義; 方炳昌
Original assignee: 中國鋼鐵股份有限公司
Priority date: 2018-09-10
Filing date: 2018-09-10
Publication date: 2020-03-16
Also published as: TWI646205B

Abstract

The present invention relates to an aluminum magnesium alloy and a method for producing the same. An aluminum raw material is firstly subjected to a casting molding process to form an aluminum billet. Next, a hot rolling process and a cold rolling process are performed to the aluminum billet to form an aluminum coil, and then the aluminum coil is subjected to an annealing process, thereby producing the aluminum magnesium alloy with excellent bending property.

Description

鋁鎂合金及其製作方法 Aluminum magnesium alloy and manufacturing method thereof

本發明係有關一種鋁鎂合金，特別是提供一種具有良好彎折性之鋁鎂合金與其製作方法。 The invention relates to an aluminum-magnesium alloy, in particular to provide an aluminum-magnesium alloy with good bendability and a manufacturing method thereof.

由於鋁鎂矽合金與鋁鎂合金具有質輕、抗腐蝕與強度佳等優點，故鋁鎂矽合金與鋁鎂合金常被應用於汽車工業，以包覆鋼材。因此，為了良好地包覆鋼材，鋁鎂矽合金與鋁鎂合金須具有良好之彎折性。若鋁鎂矽合金與鋁鎂合金不具有良好之彎折性時，彎折位置將產生大量之裂紋，而易由彎折位置破裂損壞，進而降低鋁鎂矽合金與鋁鎂合金對於鋼材之保護，且易降低其外觀品質。 Since aluminum magnesium silicon alloy and aluminum magnesium alloy have the advantages of light weight, corrosion resistance and good strength, so aluminum magnesium silicon alloy and aluminum magnesium alloy are often used in the automotive industry to clad steel. Therefore, in order to coat the steel well, the aluminum-magnesium-silicon alloy and the aluminum-magnesium alloy must have good bending properties. If the aluminum-magnesium-silicon alloy and the aluminum-magnesium alloy do not have good bending properties, a large number of cracks will be generated at the bending position, which is easy to be broken and damaged by the bending position, thereby reducing the protection of the aluminum-magnesium-silicon alloy and the aluminum-magnesium alloy for steel , And easy to reduce its appearance quality.

由於鋁鎂矽合金係熱處理型合金，故當鋁鎂矽合金經熱處理後，其易析出細微之鋁鎂矽析出相，而大幅提升鋁鎂矽合金之強度，但其彎折性較差。故，為了提升鋁鎂矽合金之彎折性，一種習知技術係調整熱處理製程，以控制析出相之尺寸與數量，而可提升所製得鋁鎂矽合金之彎折性。另一種習知技術則係控制熱處理製程之條件，以調整所形成之晶粒的結晶方位，而可增加有利於彎折方向之晶粒數量，進而提升彎折性。 Since the aluminum-magnesium-silicon alloy is a heat-treated alloy, when the aluminum-magnesium-silicon alloy is heat-treated, it is likely to precipitate fine aluminum-magnesium-silicon precipitation phases, which greatly improves the strength of the aluminum-magnesium-silicon alloy, but its bendability is poor. Therefore, in order to improve the bendability of the aluminum-magnesium-silicon alloy, a conventional technique is to adjust the heat treatment process to control the size and number of precipitated phases, which can improve the bendability of the prepared aluminum-magnesium-silicon alloy. Another conventional technique is to control the conditions of the heat treatment process in order to adjust the crystal orientation of the formed crystal grains, which can increase the number of crystal grains that are beneficial to the bending direction, thereby improving the bendability.

然而，對屬於非熱處理型合金之鋁鎂合金，其無法藉由調整熱處理製程控制晶粒數量與結晶方位。因此，習知技術一般係藉由增加鋁鎂合金之鎂含量，以於彎折過程中具有較佳之成形性，而可避免彎折位置產生裂紋。惟，為了滿足各種應用之需求，鋁鎂合金中之鎂含量亦須滿足特定之添加量。故，藉由調整鎂含量，以提升彎折性之技術手段無法適用於各種規格之鋁鎂合金，而降低其應用價值。 However, for aluminum-magnesium alloys that are not heat-treated alloys, the number of crystal grains and crystal orientation cannot be controlled by adjusting the heat treatment process. Therefore, the conventional technology generally increases the magnesium content of the aluminum-magnesium alloy to have better formability during the bending process, and can avoid cracks at the bending position. However, in order to meet the needs of various applications, the magnesium content of the aluminum-magnesium alloy must also meet a specific amount of addition. Therefore, by adjusting the magnesium content, the technical means to improve the bendability cannot be applied to aluminum-magnesium alloys of various specifications, which reduces its application value.

有鑑於此，亟須提供一種鋁鎂合金及其製作方法，以改進習知鋁鎂合金及其製作方法的缺陷。 In view of this, there is an urgent need to provide an aluminum-magnesium alloy and its manufacturing method to improve the defects of the conventional aluminum-magnesium alloy and its manufacturing method.

因此，本發明之一態樣是在提供一種鋁鎂合金的製作方法，此製作方法藉由特定之冷軋製程與退火製程，使鋁鎂合金中之結晶尺寸更為細緻，而可有效提升所製得鋁鎂合金之彎折性。 Therefore, one aspect of the present invention is to provide a method for manufacturing an aluminum-magnesium alloy. The manufacturing method uses a specific cold rolling process and an annealing process to make the crystal size in the aluminum-magnesium alloy more detailed, which can effectively improve the The bendability of the aluminum-magnesium alloy is obtained.

本發明之另一態樣是提供一種鋁鎂合金，其係利用前述之製作方法所製得。 Another aspect of the present invention is to provide an aluminum-magnesium alloy, which is manufactured by the foregoing manufacturing method.

根據本發明之一態樣，提出一種鋁鎂合金的製作方法。此鋁鎂合金的製作方法係先提供鋁合金原料，並對此鋁合金原料進行澆鑄成型製程，以形成鋁胚料。其中，鋁合金原料包含2.5重量百分比至6重量百分比之鎂、0.02重量百分比至0.5重量百分比之銅、0.05重量百分比至0.3重量百分比之錳、0.05重量百分比至0.35重量百分比之鐵、0.05重量百分比至0.2重量百分比之矽，及平衡量之鋁。 According to one aspect of the present invention, a method for manufacturing an aluminum-magnesium alloy is proposed. The manufacturing method of the aluminum-magnesium alloy is to firstly provide aluminum alloy raw materials, and to perform a casting molding process on the aluminum alloy raw materials to form aluminum blanks. Among them, the aluminum alloy raw material includes 2.5 wt% to 6 wt% magnesium, 0.02 wt% to 0.5 wt% copper, 0.05 wt% to 0.3 wt% manganese, 0.05 wt% to 0.35 wt% iron, 0.05 wt% to 0.2 weight percent silicon, and a balanced amount of aluminum.

然後，對所形成之鋁胚料進行熱軋延製程，以形成熱軋鋁捲。接著，對熱軋鋁捲進行冷軋延製程，並對所形成之冷軋鋁捲進行退火製程，即可製得本發明之鋁鎂合金。其中，冷軋延製程之軋延量係大於70%且小於或等於80%，退火製程之退火溫度係大於或等於400℃且小於450℃，且退火製程之升溫速率係大於5℃/sec。 Then, the formed aluminum blank is subjected to a hot rolling process to form a hot rolled aluminum coil. Next, the hot rolled aluminum coil is subjected to a cold rolling extension process, and the formed cold rolled aluminum coil is subjected to an annealing process to obtain the aluminum-magnesium alloy of the present invention. Among them, the rolling amount of the cold rolling process is greater than 70% and less than or equal to 80%, the annealing temperature of the annealing process is greater than or equal to 400°C and less than 450°C, and the heating rate of the annealing process is greater than 5°C/sec.

依據本發明之一實施例，前述熱軋延製程之完軋溫度為260℃至320℃，並維持熱軋延製程之最末道軋延的出口軋延量為50%至70%。 According to an embodiment of the present invention, the finish rolling temperature of the aforementioned hot rolling process is 260°C to 320°C, and the exit rolling amount of the last pass of the hot rolling process is maintained at 50% to 70%.

依據本發明之另一實施例，前述之升溫速率為5℃/sec至55℃/sec。 According to another embodiment of the present invention, the aforementioned temperature increase rate is 5°C/sec to 55°C/sec.

依據本發明之又一實施例，於進行前述之退火製程後，此製作方法可選擇性地進行水淬製程，以製得鋁鎂合金。 According to yet another embodiment of the present invention, after the aforementioned annealing process is performed, the manufacturing method may selectively perform a water quenching process to obtain an aluminum-magnesium alloy.

依據本發明之再一實施例，前述鋁鎂合金之晶粒尺寸為10μm至30μm。 According to still another embodiment of the present invention, the grain size of the aforementioned aluminum-magnesium alloy is 10 μm to 30 μm.

根據本發明之另一態樣，提出一種鋁鎂合金。此鋁鎂合金係利用前述之製作方法所製得。 According to another aspect of the present invention, an aluminum-magnesium alloy is proposed. This aluminum-magnesium alloy is made by the aforementioned manufacturing method.

應用本發明鋁鎂合金及其製作方法，其藉由提升退火製程之升溫速率，而使冷壓延製程所施加之應變能有效轉變為退火階段之再結晶的成核力，進而可細化所製得之鋁鎂合金的結晶性質，因此提升其彎折性。 By applying the aluminum-magnesium alloy of the present invention and its manufacturing method, by increasing the heating rate of the annealing process, the strain energy applied by the cold rolling process can be effectively transformed into the nucleation force of the recrystallization in the annealing stage, which can further refine the manufacturing process The resulting crystalline nature of the aluminum-magnesium alloy thus improves its bendability.

100‧‧‧方法 100‧‧‧Method

110‧‧‧提供鋁合金原料之步驟 110‧‧‧Provide aluminum alloy raw materials

120‧‧‧進行澆鑄成型製程之步驟 120‧‧‧ Steps of casting process

130‧‧‧進行熱軋延製程之步驟 130‧‧‧Procedure for hot rolling extension process

140‧‧‧進行冷軋延製程之步驟 140‧‧‧ Steps of cold rolling extension process

150‧‧‧進行退火製程之步驟 150‧‧‧Steps of annealing process

160‧‧‧形成鋁鎂合金之步驟 160‧‧‧Step of forming aluminum-magnesium alloy

為了對本發明之實施例及其優點有更完整之理解，現請參照以下之說明並配合相應之圖式。必須強調的是，各種特徵並非依比例描繪且僅係為了圖解目的。相關圖式內容說明如下：〔圖1〕係繪示依照本發明之一實施例之鋁鎂合金之製作方法的流程圖。 In order to have a more complete understanding of the embodiments of the present invention and its advantages, please refer to the following description and cooperate with the corresponding drawings. It must be emphasized that the various features are not drawn to scale and are for illustration purposes only. The contents of the related drawings are described as follows: [FIG. 1] is a flowchart showing a method for manufacturing an aluminum-magnesium alloy according to an embodiment of the present invention.

〔圖2A〕係顯示依照本發明之實施例1之鋁鎂合金的光學顯微鏡照片。 [FIG. 2A] An optical microscope photograph showing an aluminum-magnesium alloy according to Example 1 of the present invention.

〔圖2B〕係顯示依照本發明之比較例1之鋁鎂合金的光學顯微鏡照片。 [FIG. 2B] An optical microscope photograph showing an aluminum-magnesium alloy according to Comparative Example 1 of the present invention.

以下仔細討論本發明實施例之製造和使用。然而，可以理解的是，實施例提供許多可應用的發明概念，其可實施於各式各樣的特定內容中。所討論之特定實施例僅供說明，並非用以限定本發明之範圍。 The manufacture and use of embodiments of the present invention are discussed in detail below. However, it can be understood that the embodiments provide many applicable inventive concepts that can be implemented in a variety of specific contents. The specific embodiments discussed are for illustration only and are not intended to limit the scope of the invention.

請參照圖1，其係繪示依照本發明之一實施例之鋁鎂合金之製作方法的流程圖。於方法100中，鋁合金原料係先被提供，並對此鋁合金原料進行澆鑄成型製程，如步驟110與步驟120所示。在一些實施例中，基於鋁合金原料為100重量百分比，此鋁合金原料包含2.5重量百分比至6重量百分比之鎂、0.02重量百分比至0.5重量百分比之銅、0.05 重量百分比至0.3重量百分比之錳、0.05重量百分比至0.35重量百分比之鐵、0.05重量百分比至0.2重量百分比之矽，及平衡量之鋁。 Please refer to FIG. 1, which is a flowchart illustrating a method of manufacturing an aluminum-magnesium alloy according to an embodiment of the present invention. In the method 100, the aluminum alloy raw material is first provided, and the aluminum alloy raw material is subjected to a casting process, as shown in steps 110 and 120. In some embodiments, based on the aluminum alloy raw material is 100 weight percent, the aluminum alloy raw material includes 2.5 weight percent to 6 weight percent magnesium, 0.02 weight percent to 0.5 weight percent copper, 0.05 weight percent to 0.3 weight percent manganese, 0.05 weight percent to 0.35 weight percent iron, 0.05 weight percent to 0.2 weight percent silicon, and a balanced amount of aluminum.

於澆鑄成型製程中，前述之鋁合金原料係被加熱熔融，以澆鑄形成鋁胚料。 In the casting molding process, the aforementioned aluminum alloy raw material is heated and melted to form an aluminum blank by casting.

然後，對鋁胚料進行熱軋延製程，如步驟130所示。其中，進行熱軋延製程時，鋁胚料之溫度可為260℃至500℃。在一些實施例中，鋁胚料可先放置於預熱爐中，以進行預熱製程。其中，預熱爐之溫度設定為470℃至540℃，且鋁胚料於預熱爐中之放置時間(即預熱製程之預熱時間)至少為2小時。若預熱時間小於2小時，由於預熱爐所施加之熱能不足以傳導至鋁胚料之心部，故鋁胚料之心部溫度較低，而使得鋁胚料不易被軋延形變，或者軋延所施加之應力易使鋁胚料產生表面缺陷，而降低其品質。在一些實施例中，預熱時間可藉由提升預熱爐之溫度縮短，惟過高之預熱溫度將大幅增加能源成本。在一些實施例中，熱軋延製程之完軋溫度可為260℃至320℃，並維持熱軋延製程之最末道軋延的出口軋延量為50%至70%，以殘留更高之熱軋應變量，而可強化後續退火再結晶之成核能力。 Then, the aluminum blank is subjected to a hot rolling process, as shown in step 130. Wherein, during the hot rolling process, the temperature of the aluminum blank can be 260°C to 500°C. In some embodiments, the aluminum blank can be placed in a preheating furnace for the preheating process. Wherein, the temperature of the preheating furnace is set at 470°C to 540°C, and the placement time of the aluminum blank in the preheating furnace (that is, the preheating time of the preheating process) is at least 2 hours. If the preheating time is less than 2 hours, because the heat energy applied by the preheating furnace is not enough to be transferred to the core of the aluminum blank, the temperature of the core of the aluminum blank is low, which makes the aluminum blank difficult to be rolled or deformed, or The stress applied by rolling tends to cause surface defects in the aluminum blank and reduce its quality. In some embodiments, the preheating time can be shortened by increasing the temperature of the preheating furnace, but an excessively high preheating temperature will greatly increase energy costs. In some embodiments, the finish rolling temperature of the hot rolling process may be 260°C to 320°C, and the exit rolling amount of the last pass of the hot rolling process is maintained at 50% to 70%, so as to leave a higher The hot rolling strain can strengthen the nucleation ability of subsequent annealing and recrystallization.

進行步驟130後，對所形成之熱軋鋁捲料進行冷軋延製程，以形成冷軋鋁捲料。其中，冷軋延製程之軋延量可為60%至80%。當冷軋延製程之軋延量為前述之範圍時，冷軋延製程之冷加工應變能有助於鋁捲料形成更均勻且更細化之晶粒組織，而使後續所製得之鋁鎂合金具有較佳之彎折性。若冷軋延製程之軋延量小於60%時，施加於鋁捲料之應變能較少，後續所製得之鋁鎂合金的晶粒尺寸較粗大，而降低鋁鎂合金之彎折性。若冷軋延製程之軋延量大於80%時，冷軋延製程所投入之設備成本將大幅增加，且較大之軋延量較易使鋁捲料表面形成表面缺陷。在一些實施例中，冷軋延製程之軋延量較佳係大於70%且小於或等於80%。在此些實施例中，前述熱軋延製程所殘留之熱軋應變量，以及此冷軋製程之軋延量(即大於70%且小於或等於80%之軋延量)可使後續退火所形成之鋁鎂合金的晶粒尺寸相當於軋延量為80%以上之冷軋延製程所製得之鋁鎂合金的晶粒尺寸。在一些實施例中，冷軋延製程之冷軋道次至少可為三次，以減少冷軋延製程之變形餘熱所引發之自退火現象。在此些實施例中，每道次之軋延量可小於30%。 After performing step 130, the formed hot rolled aluminum coil material is subjected to a cold rolling extension process to form a cold rolled aluminum coil material. Among them, the rolling reduction of the cold rolling process can be 60% to 80%. When the rolling reduction of the cold rolling rolling process is within the aforementioned range, the cold working strain energy of the cold rolling rolling process helps the aluminum coil material to form a more uniform and finer grain structure, so that the subsequent production of aluminum magnesium The alloy has better bending properties. If the rolling amount of the cold rolling process is less than 60%, the strain energy applied to the aluminum coil is less, and the grain size of the subsequent aluminum-magnesium alloy is coarser, which reduces the bendability of the aluminum-magnesium alloy. If the rolling amount of the cold rolling process is greater than 80%, the equipment cost invested in the cold rolling process will increase significantly, and the larger rolling rate is more likely to cause surface defects on the surface of the aluminum coil. In some embodiments, the rolling reduction of the cold rolling process is preferably greater than 70% and less than or equal to 80%. In these embodiments, the hot rolling strain remaining in the aforementioned hot rolling process, and the rolling amount of the cold rolling process (that is, the rolling amount greater than 70% and less than or equal to 80%) can enable subsequent annealing The grain size of the formed aluminum-magnesium alloy is equivalent to the grain size of the aluminum-magnesium alloy produced by the cold rolling process with a rolling reduction of 80% or more. In some embodiments, the number of cold rolling passes in the cold rolling process can be at least three times to reduce the self-annealing phenomenon caused by the deformation residual heat of the cold rolling process. In these embodiments, the rolling reduction per pass may be less than 30%.

接著，對冷軋鋁捲料進行退火製程，即可形成鋁鎂合金，如步驟150與步驟160所示。其中，退火製程之升溫速率係大於5℃/sec，且退火溫度為400℃至550℃。當冷軋鋁捲料進行退火製程時，前述冷軋延製程施加於冷軋鋁捲料之冷加工應變能可轉變為再結晶之成核力，而有助於使冷軋鋁捲料中之晶粒形成尺寸較細緻之晶粒，進而可提升所製得鋁鎂合金之彎折性。 Next, an annealing process is performed on the cold-rolled aluminum coil material to form an aluminum-magnesium alloy, as shown in steps 150 and 160. Among them, the heating rate of the annealing process is greater than 5°C/sec, and the annealing temperature is 400°C to 550°C. When the cold-rolled aluminum coil material is annealed, the cold-worked strain energy applied to the cold-rolled aluminum coil material in the aforementioned cold-rolling extension process can be converted into a nucleating force for recrystallization, which helps to make the crystals in the cold-rolled aluminum coil material The grains form finer grains, which in turn can improve the bendability of the prepared aluminum-magnesium alloy.

若升溫速率不大於5℃/sec時，冷軋延製程之冷加工應變能無法有效轉變為再結晶之成核力，而使所形成之鋁鎂合金的晶粒尺寸較粗大，而降低所形成之鋁鎂合金的彎折性。若退火溫度不為前述之範圍時，此退火溫度所進行之退火製程不易使冷軋鋁捲料中之晶粒再結晶為所要求之晶粒結構或晶粒尺寸，而難以製得符合需求之鋁鎂合金。再者，若退火溫度小於400℃時，過低之退火溫度不利於冷軋鋁捲料中之晶粒再結晶，而降低所製得鋁鎂合金之結晶性質。若退火溫度大於550℃時，過高之退火溫度將使晶粒尺寸過度成長，而降低鋁鎂合金之彎折性。 If the heating rate is not greater than 5°C/sec, the cold working strain energy of the cold rolling process cannot be effectively converted into the nucleation force of recrystallization, which makes the grain size of the formed aluminum-magnesium alloy coarser and reduces the formed Bending property of aluminum-magnesium alloy. If the annealing temperature is not within the aforementioned range, the annealing process performed at this annealing temperature is not easy to recrystallize the grains in the cold-rolled aluminum coil into the required grain structure or grain size, and it is difficult to produce a product that meets the requirements Aluminum-magnesium alloy. Furthermore, if the annealing temperature is less than 400°C, an excessively low annealing temperature is not conducive to recrystallization of the crystal grains in the cold-rolled aluminum coil material, and reduces the crystallinity of the prepared aluminum-magnesium alloy. If the annealing temperature is greater than 550°C, an excessively high annealing temperature will cause the grain size to grow excessively and reduce the bendability of the aluminum-magnesium alloy.

在一些實施例中，退火製程之升溫速率可為5℃/sec至55℃/sec。當退火製程之升溫速率為5℃/sec至55℃/sec時，基於設備所耗費之成本而言，冷加工應變能轉變為再結晶之成核力的效果係較佳的。換言之，為兼顧應變能轉換為成核力之效果與設備成本，5℃/sec至55℃/sec之升溫速率係較佳參數。 In some embodiments, the heating rate of the annealing process may be 5°C/sec to 55°C/sec. When the heating rate of the annealing process is 5°C/sec to 55°C/sec, based on the cost of the equipment, the effect of transforming cold work strain energy into nucleation force for recrystallization is better. In other words, in order to balance the effect of conversion of strain energy into nucleation force and equipment cost, a heating rate of 5°C/sec to 55°C/sec is a preferred parameter.

在一些實施例中，退火溫度較佳可大於或等於400℃且小於500℃，且更佳係大於或等於400℃且小於450℃。 In some embodiments, the annealing temperature may preferably be greater than or equal to 400°C and less than 500°C, and more preferably be greater than or equal to 400°C and less than 450°C.

在一些實施例中，於進行退火製程後，此製作方法可選擇性地對退火後之鋁捲料進行水淬製程，以形成鋁鎂合金。當利用水淬製程來冷卻退火後之鋁捲料時，水淬製程之快速降溫有助於使鋁捲料之晶粒被維持為具有適當晶粒尺寸，而可避免因冷卻速度過慢所導致之晶粒尺寸增大，因此可提升所製得鋁鎂合金之彎折性。 In some embodiments, after the annealing process, the manufacturing method can selectively perform a water quenching process on the annealed aluminum coil to form an aluminum-magnesium alloy. When the water quenching process is used to cool the annealed aluminum coil, the rapid cooling of the water quenching process helps to maintain the grains of the aluminum coil to an appropriate grain size, which can avoid the slow cooling rate. The grain size increases, so the bendability of the prepared aluminum-magnesium alloy can be improved.

在一具體例中，藉由前述方法所製得之鋁鎂合金的晶粒尺寸可為10μm至30μm，而可具有良好之彎折性。 In a specific example, the grain size of the aluminum-magnesium alloy produced by the foregoing method may be 10 μm to 30 μm, and may have good bendability.

以下利用實施例以說明本發明之應用，然其並非用以限定本發明，任何熟習此技藝者，在不脫離本發明之精神和範圍內，當可作各種之更動與潤飾。 The following examples are used to illustrate the application of the present invention, but it is not intended to limit the present invention. Anyone who is familiar with this art can make various changes and modifications without departing from the spirit and scope of the present invention.

製備鋁合金原料Preparation of aluminum alloy raw materials 製備例1Preparation Example 1

基於製備例1之鋁合金原料為100重量百分比，其包含2.9重量百分比之鎂、0.02重量百分比之銅、0.11重量百分比之錳、0.3重量百分比之鐵、0.17重量百分比之矽，以及餘量的鋁。 The aluminum alloy raw material based on Preparation Example 1 is 100% by weight, which includes 2.9% by weight of magnesium, 0.02% by weight of copper, 0.11% by weight of manganese, 0.3% by weight of iron, 0.17% by weight of silicon, and the balance of aluminum .

製備例2Preparation Example 2

基於製備例2之鋁合金原料為100重量百分比，其包含4.3重量百分比之鎂、0.4重量百分比之銅、0.22重量百分比之錳、0.17重量百分比之鐵、0.1重量百分比之矽，以及餘量的鋁。 The aluminum alloy raw material based on Preparation Example 2 is 100 weight percent, which includes 4.3 weight percent magnesium, 0.4 weight percent copper, 0.22 weight percent manganese, 0.17 weight percent iron, 0.1 weight percent silicon, and the balance aluminum .

製備例3Preparation Example 3

基於製備例3之鋁合金原料為100重量百分比，其包含5.5重量百分比之鎂、0.35重量百分比之銅、0.25重量百分比之錳、0.1重量百分比之鐵、0.15重量百分比之矽，以及餘量的鋁。 The aluminum alloy raw material based on Preparation Example 3 is 100 weight percent, which includes 5.5 weight percent magnesium, 0.35 weight percent copper, 0.25 weight percent manganese, 0.1 weight percent iron, 0.15 weight percent silicon, and the balance aluminum .

製備鋁鎂合金Preparation of aluminum-magnesium alloy 實施例1Example 1

首先，對製備例1之鋁合金原料進行澆鑄成型製程，以製得鋁胚料。然後，對鋁胚料進行熱軋延製程與冷軋延製程，以形成冷軋鋁捲料，且冷軋延製程之軋延量為75%。進一步地，對此冷軋鋁捲料進行退火製程，即可製得實施例1之鋁鎂合金。其中，退火製程之退火溫度為420℃。所得之鋁鎂合金以下述降伏強度、伸長率與彎折性之評價方式進行評價，其中降伏強度、伸長率與彎折性之評價結果如第1表所示。 First, the aluminum alloy raw material of Preparation Example 1 is subjected to a casting process to obtain an aluminum blank. Then, the aluminum blank is subjected to a hot rolling process and a cold rolling process to form a cold rolled aluminum coil, and the rolling amount of the cold rolling process is 75%. Further, by performing an annealing process on this cold-rolled aluminum coil, the aluminum-magnesium alloy of Example 1 can be obtained. The annealing temperature of the annealing process is 420°C. The obtained aluminum-magnesium alloy was evaluated according to the following evaluation methods of yield strength, elongation, and bendability. The evaluation results of yield strength, elongation, and bendability are shown in Table 1.

實施例2至實施例3與比較例1Example 2 to Example 3 and Comparative Example 1

實施例2至實施例3與比較例1之鋁鎂合金係使用與實施例1之鋁鎂合金的製作方法相同之流程步驟，不同之處在於實施例2至實施例3與比較例1係使用不同之鋁合金原料及/或不同之冷軋延製程的軋延量與退火溫度，且其條件如第1表所示。其中，實施例2至實施例3與比較例1所製得之鋁鎂合金分別以下述降伏強度、伸長率與彎折性之評價方式進行評價，且其結果如第1表所示。 The aluminum-magnesium alloys of Examples 2 to 3 and Comparative Example 1 use the same process steps as the manufacturing method of the aluminum-magnesium alloy of Example 1, except that Examples 2 to 3 and Comparative Example 1 are used The rolling amount and annealing temperature of different aluminum alloy raw materials and/or different cold rolling processes are shown in Table 1. Among them, the aluminum-magnesium alloys prepared in Examples 2 to 3 and Comparative Example 1 were evaluated by the following evaluation methods of yield strength, elongation, and bendability, and the results are shown in Table 1.

評價方式Evaluation method 1.降伏強度1. Yield Strength

實施例1至實施例3與比較例1所製得鋁鎂合金之降伏強度係利用本案所屬技術領域具有通常知識者所熟知之儀器與方法來量測，故在此不另贅述。 The yield strengths of the aluminum-magnesium alloys prepared in Examples 1 to 3 and Comparative Example 1 are measured using instruments and methods well known to those of ordinary skill in the technical field to which this case belongs, so they are not described here.

2.伸長率2. Elongation

實施例1至實施例3與比較例1之鋁鎂合金的伸長率係依據日本工業規格(Japanese Industrial Standards；JIS)之JIS Z2241所載的伸長率試驗方法來量測所製得鋁鎂合金之伸長率。 The elongation rates of the aluminum-magnesium alloys of Examples 1 to 3 and Comparative Example 1 are measured according to the elongation test method contained in JIS Z2241 of Japanese Industrial Standards (JIS) Elongation.

3.彎折性3. Bending

實施例1至實施例3與比較例1之鋁鎂合金的彎折性係將所製得之鋁鎂合金板進行彎折試驗，並以目視之方式觀察鋁鎂合金板的外表面之彎折處是否有裂紋。 The bendability of the aluminum-magnesium alloys of Examples 1 to 3 and Comparative Example 1 is to perform a bending test on the prepared aluminum-magnesium alloy plate, and observe the bending of the outer surface of the aluminum-magnesium alloy plate visually Are there any cracks?

其中，彎折試驗係將鋁鎂合金板彎折180度，並使彎折後之兩內表面間的距離為一個設定厚度。須說明的是，依據應用領域之不同，此設定厚度可隨之調整。舉例而言，當所製得之鋁鎂合金板欲包覆厚度為t之板材時，彎折試驗即係將鋁鎂合金板彎折180度，並使彎折後之兩內表面間的距離為t。 Among them, the bending test is to bend the aluminum-magnesium alloy plate 180 degrees, and make the distance between the two inner surfaces after bending to a set thickness. It should be noted that, depending on the application field, this set thickness can be adjusted accordingly. For example, when the prepared aluminum-magnesium alloy plate is to be coated with a thickness of t, the bending test is to bend the aluminum-magnesium alloy plate 180 degrees, and the distance between the two inner surfaces after bending Is t.

依據第1表所載之結果可知，實施例1至實施例3所製得之鋁鎂合金具有10μm至30μm之晶粒尺寸，且其彎折後之表面不具有裂紋，顯見實施例1至實施例3之鋁鎂合金具有良好之彎折性。 According to the results shown in Table 1, the aluminum-magnesium alloys prepared in Examples 1 to 3 have a grain size of 10 μm to 30 μm, and the surface after bending does not have cracks, which is obvious from Example 1 to implementation The aluminum-magnesium alloy of Example 3 has good bendability.

另外，請參照圖2A與圖2B，其中圖2A係顯示依照本發明之實施例1之鋁鎂合金的光學顯微鏡照片，圖2B係顯示依照本發明之比較例1之鋁鎂合金的光學顯微鏡照片，且圖2A與圖2B之比例尺規均代表500μm。依據光學顯微鏡之晶相照片可知，實施例1之鋁鎂合金具有較細緻之晶粒尺寸，且實施例1之鋁鎂合金具有較多數量之結晶顆粒；但實施例2之鋁鎂合金具有較大之晶粒尺寸，且具有較少之結晶顆粒。因此，當實施例1與實施例2之鋁鎂合金彎折時，由於實施例2之鋁鎂合金的晶粒尺寸較大，故鋁鎂合金易沿著晶粒邊界形成裂紋，而具有較差之彎折性。 In addition, please refer to FIGS. 2A and 2B, wherein FIG. 2A is an optical microscope photograph of an aluminum-magnesium alloy according to Example 1 of the present invention, and FIG. 2B is an optical microscope photograph of an aluminum-magnesium alloy according to Comparative Example 1 of the present invention. , And the scale rule of FIG. 2A and FIG. 2B both represent 500 μm. According to the crystal phase photo of the optical microscope, the aluminum-magnesium alloy of Example 1 has a finer grain size, and the aluminum-magnesium alloy of Example 1 has a larger number of crystalline particles; but the aluminum-magnesium alloy of Example 2 has a better Large grain size and less crystal particles. Therefore, when the aluminum-magnesium alloys of Example 1 and Example 2 are bent, since the grain size of the aluminum-magnesium alloy of Example 2 is larger, the aluminum-magnesium alloy is prone to form cracks along the grain boundaries, and has a poorer Bending.

據此，本發明之鋁鎂合金的製作方法藉由特定之冷軋延製程與退火製程可使所製得之鋁鎂合金的晶粒更為細緻且均勻，而可提升鋁鎂合金之彎折性。 According to this, the manufacturing method of the aluminum-magnesium alloy of the present invention can make the grains of the prepared aluminum-magnesium alloy more detailed and uniform through a specific cold rolling and annealing process, and can improve the bending of the aluminum-magnesium alloy Sex.

雖然本發明已以實施方式揭露如上，然其並非用以限定本發明，在本發明所屬技術領域中任何具有通常知識者，在不脫離本發明之精神和範圍內，當可作各種之更動與潤飾，因此本發明之保護範圍當視後附之申請專利範圍所界定者為準。 Although the present invention has been disclosed as above in the embodiments, it is not intended to limit the present invention. Anyone with ordinary knowledge in the technical field to which the present invention belongs can make various modifications and changes without departing from the spirit and scope of the present invention. Retouching, therefore, the protection scope of the present invention shall be subject to the scope defined in the appended patent application.

100‧‧‧方法 100‧‧‧Method

150‧‧‧進行退火製程之步驟 150‧‧‧Steps of annealing process

Claims

一種鋁鎂合金的製作方法，包含：提供一鋁合金原料，其中該鋁合金原料包含2.5重量百分比至6重量百分比之鎂、0.02重量百分比至0.5重量百分比之銅、0.05重量百分比至0.3重量百分比之錳、0.05重量百分比至0.35重量百分比之鐵、0.05重量百分比至0.2重量百分比之矽，及平衡量之鋁；對該鋁合金原料進行一澆鑄成型製程，以形成一鋁胚料；對該鋁胚料進行一熱軋延製程，以形成一熱軋鋁捲料；對該熱軋鋁捲料進行一冷軋延製程，以形成一冷軋鋁捲料，其中該冷軋延製程之一軋延量係大於70%且小於或等於80%；以及對該冷軋鋁捲料進行一退火製程，以形成該鋁鎂合金，其中該退火製程之一退火溫度係大於或等於400℃且小於450℃，且該退火製程之一升溫速率大於5℃/sec。 A method for manufacturing an aluminum-magnesium alloy, comprising: providing an aluminum alloy raw material, wherein the aluminum alloy raw material includes 2.5 to 6 weight percent magnesium, 0.02 to 0.5 weight percent copper, and 0.05 to 0.3 weight percent Manganese, 0.05% by weight to 0.35% by weight iron, 0.05% by weight to 0.2% by weight silicon, and a balanced amount of aluminum; a casting molding process is performed on the aluminum alloy raw material to form an aluminum blank; the aluminum blank The material is subjected to a hot rolling process to form a hot rolled aluminum coil; the hot rolled aluminum coil is subjected to a cold rolling process to form a cold rolled aluminum coil, wherein one of the cold rolling processes is rolled The amount is greater than 70% and less than or equal to 80%; and an annealing process is performed on the cold-rolled aluminum coil to form the aluminum-magnesium alloy, wherein an annealing temperature of one of the annealing processes is greater than or equal to 400°C and less than 450°C , And one of the annealing process heating rate is greater than 5 ℃/sec.

如申請專利範圍第1項所述之鋁鎂合金的製作方法，其中該熱軋延製程之一完軋溫度為260℃至320℃，並維持該熱軋延製程之一最末道軋延的一出口軋延量為50%至70%。 The method for manufacturing an aluminum-magnesium alloy as described in item 1 of the patent application scope, wherein the finish rolling temperature of one of the hot rolling rolling processes is 260°C to 320°C, and the last rolling of one of the hot rolling rolling processes is maintained An export rolling volume is 50% to 70%.

如申請專利範圍第1項所述之鋁鎂合金的製作方法，其中該升溫速率為5℃/sec至55℃/sec。 The method for manufacturing an aluminum-magnesium alloy as described in item 1 of the patent application range, wherein the temperature increase rate is 5°C/sec to 55°C/sec.

如申請專利範圍第1項所述之鋁鎂合金的製作方法，於進行該退火製程後，該製作方法更包含：進行一水淬製程，以製得該鋁鎂合金。 According to the method for manufacturing an aluminum-magnesium alloy described in item 1 of the patent application scope, after the annealing process is performed, the manufacturing method further includes: performing a water quenching process to obtain the aluminum-magnesium alloy.

如申請專利範圍第1項所述之鋁鎂合金的製作方法，其中該鋁鎂合金之一晶粒尺寸為10μm至30μm。 The method for manufacturing an aluminum-magnesium alloy as described in item 1 of the patent application range, wherein one of the aluminum-magnesium alloys has a grain size of 10 μm to 30 μm.

一種鋁鎂合金，藉由如申請專利範圍第1至5項中之任一項所述之製作方法所製得。 An aluminum-magnesium alloy produced by the manufacturing method as described in any one of patent application items 1 to 5.